US20070232476A1 - Transparent glass ceramic plate that has an opaque, colored bottom coating over the entire surface or over part of the surface - Google Patents

Transparent glass ceramic plate that has an opaque, colored bottom coating over the entire surface or over part of the surface Download PDF

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US20070232476A1
US20070232476A1 US11/688,099 US68809907A US2007232476A1 US 20070232476 A1 US20070232476 A1 US 20070232476A1 US 68809907 A US68809907 A US 68809907A US 2007232476 A1 US2007232476 A1 US 2007232476A1
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glass ceramic
ceramic plate
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Friedrich Siebers
Ulrich Schiffner
Wolfgang Schmidbauer
Klaus Schonberger
Petra Grewer
Erich Rodek
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Schott AG
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Schott AG
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    • 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
    • C03C3/095—Glass compositions containing silica with 40% to 90% silica, by weight containing rare earths
    • 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
    • C03C10/00—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition
    • C03C10/0018—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing SiO2, Al2O3 and monovalent metal oxide as main constituents
    • C03C10/0027—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing SiO2, Al2O3 and monovalent metal oxide as main constituents containing SiO2, Al2O3, Li2O as main constituents
    • 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
    • C03C10/00—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition
    • C03C10/0036—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing SiO2, Al2O3 and a divalent metal oxide as main constituents
    • C03C10/0045—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing SiO2, Al2O3 and a divalent metal oxide as main constituents containing SiO2, Al2O3 and MgO as main constituents
    • 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
    • C03C10/00—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition
    • C03C10/0054—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing PbO, SnO2, B2O3

Definitions

  • the invention relates to a transparent glass ceramic plate with high-quartz mixed crystals as the prevailing crystal phase, which is exposed to operationally high thermal stresses and which has an opaque, colored, high-temperature-stable bottom coating over the entire surface or over part of the surface.
  • glass ceramic plates are to be defined as not only flat, smooth plates, but also plates that are deformed three-dimensionally, such as, e.g., beveled, angled or curved plates.
  • the plates can be designed rectangular or round or can also have another shape.
  • Such glass ceramic plates have a very low thermal expansion coefficient in the temperature range between room temperature up to 700° C. of usually ⁇ 20/700 ⁇ 1.5 ⁇ 10 ⁇ 6 /K and thus high temperature resistance and temperature gradient strength. They are used in transparent form, e.g., as fire protection glass, fireplace door windows and cooking surfaces.
  • the glass ceramic cooking surfaces are reduced in their light transmission to values of about 0.5 to 10%. This can take place, on the one hand, by additions of coloring elements by absorption, as is described in, for example, EP 220333. These glass ceramic cooking surfaces then appear black when viewed from above and red-violet or orange-brown when looking through depending on the coloring elements that are used.
  • panes Another application of the glass ceramic panes exists in the use as, e.g., fireplace door windows.
  • the panes must be transparent.
  • panes of the same composition could be used for these two applications.
  • a comparatively new technical approach for the production of cooking surfaces consists in making transparent glass ceramic plates optically non-transparent by an opaque, colored bottom coating.
  • the bottom coating is optionally partially interrupted by providing optically transparent areas for displays, e.g., LED or LCD displays of residual heat in the cooking zones.
  • optically transparent areas for displays, e.g., LED or LCD displays of residual heat in the cooking zones.
  • color or black-white screen displays e.g., for showing cooking recipes or for interactive functions (Internet, integration with other household appliances, control electronics) can be integrated under the optically transparent areas.
  • Transparent, non-colored stove tops which are provided with a bottom coating
  • a bottom coating are known from, e.g., U.S. Pat. No. 6,914,223 B2, US 2005/0129959 A1 or U.S. Pat. No. 6,660,989 B2.
  • the type and structure of the bottom coating can be designed differently in the colder and hotter areas, e.g., in the cooking zones of the cooking surfaces.
  • luster paints organic-based paints, glass-flux-based decorative paints with coloring pigments and colored or pigmented sol-gel layers are mentioned.
  • pigments conventional inorganic pigments, luster pigments, metal effect pigments or pearlescent interference pigments and various mixtures of these pigments are used.
  • the transparent glass ceramic plate So that the color of the bottom coating is not altered by the transparent glass ceramic plate, it is advantageous if the latter has a low inherent color. Since the irradiating light passes through the glass ceramic plate before it falls on the colored coating to be partially absorbed and reflected on the latter, before it then passes back again through the glass ceramic plate and reaches the observer, a weak inherent color of the transparent glass ceramic plate also has a disruptive effect. The advantages of a transparent glass ceramic plate with low inherent color are found in the prior art.
  • U.S. Pat. No. 6,914,223 B2 describes how a new color shade is set by superposition of the colors of the bottom coating with the brownish-yellow inherent coloring of the glass ceramic plate. It is disadvantageous that the recognizable inherent color of the transparent glass ceramic plate depends on the thickness thereof. In addition, certain pure color shades, e.g., white or silver-metallic, cannot be produced for the observer without an unsettling brown-yellow color hue. In the development of a color palette of various colored bottom coatings, it is necessary always to consider the inherent color of the transparent glass ceramic plates. For the observer, this inherent color is, however, as explained, dependent on the thickness of the glass ceramic plates and can also vary by process-induced fluctuations (raw material contamination, melt conditions, glazing). For the above-mentioned reasons, an effort is therefore to be made to set the inherent color in the transparent glass ceramic plate to as low a value as possible.
  • the inherent color of transparent glass ceramic plates can have various causes. Also, the use of the refining agent Sb 2 O 3 results in a low inherent color.
  • the described brownish-yellow inherent coloring of the transparent glass ceramics is based on electronic transitions to color complexes that absorb in the area of the visible light and on which the component—the Ti ion—that is necessary for the nucleation is involved. The most frequently absorbing color complex is the formation of adjacent Fe and Ti ions, between which electronic charge-transfer transitions take place. The formation of these adjacent complexes takes place as early as during cooling of the starting glass and in particular during later glazing of the glass ceramics. By preferred stratification of the ions involved in the charge transfer during glazing, the inherent color is thus quite considerably enhanced compared to the starting glass.
  • the reduction of the Fe content is a measure that is economically usable only to a certain extent, however.
  • a certain amount of Fe 2 O 3 always develops through the industrially available raw materials of the batch for the production and homogenization of the batch. Based on the costs for extremely pure raw materials and for special plant design measures, it is economically no longer justifiable to reduce the Fe 2 O 3 content below about 50 ppm in transparent glass ceramics.
  • the Fe 2 O 3 content is usually on the order of magnitude of about 150 to 500 ppm.
  • U.S. Pat. No. 4,438,210 describes approaches for reducing the Fe/Ti color complex.
  • transparent glass ceramics with low inherent color are obtained, which acquire 2-6% by weight of TiO 2 and 0-2% by weight of ZrO 2 as a nucleating agent and up to about 0.1% by weight of Fe 2 O 3 as a contaminant because the component MgO is essentially omitted.
  • the replacement of the nucleating agent TiO 2 is described in JP 03-23237 A.
  • These glass ceramics forego the addition of TiO 2 as a nucleating agent and are based on mixed nucleation by ZrO 2 /SnO 2 .
  • the SnO 2 contents that are necessary for this purpose are more than 1% by weight. In the case of these high SnO 2 contents, however, the devitrification resistance of the glass deteriorates in the area of shaping in viscosities around the processing temperature V A of 10 4 dpas.
  • V A of 10 4 dpas.
  • disruptive Sn— and/or Zr-containing crystal phases crystallize out. It thus results in an unreliable reduction of the resistance of the glass plates and the glass ceramic plates that are produced therefrom.
  • the light scattering can be determined visually on glass ceramic plates or quantitatively by measuring the turbidity (English: haze) according to ASTM D 1003.
  • nucleating agents ZrO 2 and SnO 2 are limited because of the devitrification during shaping, a minimum content of the nucleating agent TiO 2 is necessary in the current prior art to ensure the devitrification resistance during shaping of glass plates.
  • the color of the coating when looking through the transparent glass ceramic plate is not altered in color but rather is superimposed in a hardly noticeable way by a light gray hue. Since the existing absorption bands are neutralized by complementary absorption bands of the staining agent, a reduced light transmission is produced overall.
  • this results in visually recognizable remnants in the lime-sodium glass products; in the most disadvantageous case, it can result in Li 2 O—Al 2 O 3 —SiO 2 melt remnants and in the clogging of channels or nozzles in the shaping process and thus in total failure during production of lime-sodium glasses.
  • the object is therefore to find a glass ceramic plate that is coated over the entire surface or over part of the surface on the back side and that does not have any of the disruptive color shade distorting the colors of the coating on the back side and that can be clearly identified in cullet sorting facilities with optical cullet recognition.
  • a glass ceramic plate that is coated on the back side in the lithium-aluminosilicate glass system with high-quartz mixed crystals as a prevailing crystal phase was found, and said plate has an Nd 2 O 3 content of 40-4000 ppm, a Yellowness Index of less than 10% with a 4 mm plate thickness and a variegation of colors of the glass ceramic in the CIELAB color system of C* of less than 5.
  • the measurement of the Yellow Index takes place with standard illuminant C according to the ASTM Standard 1925/70 (77, 85).
  • the color coordinates L*, a*, and b* from the CIELAB system can be converted in a known way into color coordinates x, y and brightness (light transmission) Y of the CIE color system.
  • neodymium addition especially readily counteracts the color hues formed by Sb 2 O 3 refining additives and by SnTi color complexes, in addition to the color hues formed by Fe/Ti color complexes.
  • the Nd additive by itself does not shift the color point exactly in the direction of the achromatic point, such that this slight correction may be advantageous.
  • Additional fine corrections of the color site can also be performed with other staining agents, such as, e.g., Cr, Ni, V, Cu, Mn and Ce.
  • the transparent glass ceramic plate according to the invention preferably has a composition in % by weight based on oxide of: Li 2 O 3.0-4.5 Na 2 O 0-1.5 K 2 O 0-1.5 ⁇ Na 2 O + K 2 O 0.2-2.0 MgO 0-2.0 CaO 0-1.5 SrO 0-1.5 BaO 0-2.5 ZnO 0-2.5 B 2 O 3 0-1.0 Al 2 O 3 19-25 SiO 2 55-69 TiO 2 1-3 ZrO 2 1-2.5 SnO 2 0-0.4 ⁇ SnO 2 + TiO 2 ⁇ 3 P 2 O 5 0-3.0 Nd 2 O 3 0.01-0.4 CoO 0-0.004 optionally with the additions of chemical refining agents such as As 2 O 3 , Sb 2 O 3 , and CeO 2 and refining additives, such as sulfate compounds, chloride compounds, and fluoride compounds in total contents of up to 2.0% by weight.
  • chemical refining agents such as As 2 O 3 , Sb 2 O 3 , and CeO 2 and
  • the oxides Li 2 O, Al 2 O 3 and SiO 2 are components for the formation of high-quartz and/or keatite mixed crystal phases that are necessary within the preferred limits indicated in the claims.
  • Li 2 O contents of over 4.5% by weight are critical for the devitrification resistance in the production of glass ceramic plates.
  • the Al 2 O 3 content is at least 19% by weight and is limited—to avoid high viscosities of the glass and because of the undesirable devitrification of mullite phases during shaping- to a maximum 25% by weight, preferably 24% by weight.
  • the SiO 2 content is to be 55 to a maximum of 69% by weight, preferably a maximum up to 68% by weight, since this component greatly increases the viscosity of the glass. For melting the glasses and with respect to the temperature stress during shaping, higher contents of SiO 2 are therefore disadvantageous.
  • alkalis Na 2 O and K 2 O in amounts of, in each case, up to 1.5% by weight, the alkaline-earths CaO up to 1.5% by weight, SrO up to 1.5% by weight, BaO up to 2.5% by weight and B 2 O 3 up to 1% by weight improve the meltability and the devitrification behavior during shaping.
  • the contents are limited, however, since these components essentially remain in the residual glass phase of the glass ceramic and increase the thermal expansion in an unreliable way. Thus, they have a disadvantageous effect on the temperature resistance of the glass ceramic plates.
  • the sum of the alkalis Na 2 O+KO 2 is to be at least 0.2% by weight, preferably at least 0.3% by weight.
  • MgO, ZnO and P 2 O 5 can be incorporated in the crystal phase. Because of the problem of forming undesirable crystal phases with higher thermal expansion, such as, e.g., Zn spinel during glazing, the ZnO content is limited to values of at most 2.5% by weight, preferably at most 2.0% by weight. The MgO content is limited to at most 2.0, preferably 1.5% by weight, since it otherwise unreliably increases the thermal expansion of the glass ceramic. For low inherent colors, MgO contents of less than 0.8% by weight and in particular less than 0.6% by weight are advantageous. A minimum MgO content of 0.1% by weight is generally required, so that the thermal expansion of the glass ceramic between 20° C. and 700° C.
  • the addition of P 2 O 5 can be up to 3% by weight and is preferably limited to 1.5% by weight.
  • the addition of P 2 O 5 is advantageous for the devitrification resistance; higher contents have a disadvantageous effect on the acid resistance.
  • the Nd content is converted onto an oxide base (Nd 2 O 3 ), whereby the type of Nd additive in the batch is not limited to the indicated oxide, but rather any Nd compounds can be added.
  • the contents of the nucleating components TiO 2 , ZrO 2 , and SnO 2 are to be controlled within relatively narrow limits. Certain minimum contents are necessary to produce high density during the desired short glazing times of less than 2.5 hours, so that after the high-quartz mixed crystals are grown, transparent glass ceramics can be produced without disruptive turbidity.
  • TiO 2 For an effective nucleation, in any case a minimum content of TiO 2 of 1% by weight is necessary.
  • the TiO 2 content is to be a maximum of 3% by weight, preferably at most 2.7% by weight, since this component is involved in the formation of Fe/Ti and Sn/Ti color complexes that disrupt the inherent color.
  • the content of SnO 2 is not to exceed 0.4% by weight, preferably 0.3% by weight, since otherwise it results in an undesirable devitrification of an Sn-containing crystal phase during shaping close to the processing temperature V A and since the Sn/Ti color complexes contribute to the inherent color.
  • the refining agents As 2 O 3 and/or Sb 2 O 3 which are common for glass ceramics from the Li 2 O—Al 2 O 3 —SiO 2 system, can be used. These refining agents are distinguished in that they exert their refining action by releasing O 2 .
  • the use of the nucleating agent SnO2 is especially advantageous if the latter is used in addition as a refining agent in connection with a high-temperature refining of greater than 1700° C., since SnO 2 cleaves the O 2 that is required for refining at these elevated temperatures.
  • refining agent additives such as, e.g., sulfate compounds, chloride compounds and fluoride compounds, can be added to the glass melt.
  • the total content of the refining agent and refining additives is not to exceed 2% by weight.
  • the water content of the starting glasses according to the invention is usually between 0.015 and 0.06 mol/l, depending on the selection of the raw materials of the batch and the process conditions in the melt. This corresponds to ⁇ OH values of 0.16 to 0.64 mm ⁇ 1 .
  • the glass in an especially preferred embodiment contains the following in % by weight based on oxide: Li 2 O 3.2-4.3 Na 2 O 0.2-1.0 K 2 O 0-0.8 ⁇ Na 2 O + K 2 O 0.3-1.5 MgO 0.1-1.5 CaO 0-1.0 SrO 0-1.0 BaO 0-2.5 ZnO 0-2.0 Al 2 O 3 19-24 SiO 2 60-68 TiO 2 1.0-2.7 ZrO 2 1.2-2.2 SnO 2 0-0.3 ⁇ SnO 2 + TiO 2 ⁇ 2.7 P 2 O 5 0-1.5 Nd 2 O 3 200-3000 ppm CoO 0-30 ppm optionally with the additions of chemical refining agents such as As 2 O 3 , Sb 2 O 3 , and CeO 2 and refining additives such as sulfate compounds, chloride compounds, and fluoride compounds in total amounts of up to 1.5% by weight.
  • chemical refining agents such as As 2 O 3 , Sb 2 O 3 , and CeO 2
  • the glass ceramic plate contains As 2 O 3 as a refining agent, optionally with additional refining additives such as sulfate, chloride and fluoride compounds in total contents of up to 1% by weight, and is plained without the refining agents Sb 2 O 3 and SnO 2 .
  • the transparent coated glass ceramic plate according to the invention with high-quartz mixed crystals as the prevailing crystal phase is to have a thermal expansion coefficient of between room temperature and 700° C., which deviates from the zero expansion by no more than 0.5 ⁇ 10 ⁇ 6 /K. The deviation of less than 0.3 ⁇ 10 ⁇ 6 /K is to be preferred. With the low thermal expansion coefficients, a high temperature difference resistance of the glass ceramic plate is achieved.
  • the transparent glass ceramic plate according to the invention contains less than 2.5% by weight of TiO2, less than 2000 ppm of Nd 2 O 3 and less than 20 ppm of CoO, and the Fe 2 O 3 content is less than 300 ppm, preferably less than 210 ppm.
  • the transparent glass ceramic plate according to the invention contains less than 2.5% by weight of TiO2, less than 2000 ppm of Nd 2 O 3 and less than 20 ppm of CoO, and the Fe 2 O 3 content is less than 300 ppm, preferably less than 210 ppm.
  • a 4 mm thickness it is possible, with a 4 mm thickness, to achieve a light transmission of greater than 80%, preferably greater than 85%, associated with low inherent color, i.e., a Yellowness Index of less than 7% and a variegation of colors (chromaticity) in the CIELAB system C* of less than 3.5.
  • turbidity is to be less than 1%, preferably less than 0.5% (measured for a 3.6 mm-thick plate with a polished surface). According to ASTM D 1003, turbidity is the proportion, in percent, of the transmitted light, which deviates from the irradiated light beam on average by more than 2.5°.
  • nucleation action of SnO 2 and TiO 2 is about the same. Therefore, these two components can be considered together.
  • the nucleation action of the ZrO 2 (in % by weight) is clearly greater than that of TiO 2 or SnO 2 . Therefore, the combinations of nucleating agents ZrO 2 and (TiO 2 +SnO 2 ) can be produced with the same nucleating action, and said combinations follow a relationship.
  • the glass ceramic plates according to the invention can be converted into a glass ceramic that contains keatite mixed crystals by an additional temperature treatment at temperatures of between about 900 and 1200° C.
  • Glass ceramics of this type have a higher temperature resistance, but at the expense of an increase in the thermal expansion coefficient, which is between room temperature and 700° C. on the order of magnitude of about 1 ⁇ 10 ⁇ 6 /K. Because of the crystal growth that accompanies the conversion, they have a translucent to opaque-white appearance.
  • the turbidity is generally >50% in haze values.
  • the transparent coated glass ceramic plates according to the invention are suitable especially as cooking surfaces for use in a stove top.
  • the opaque, colored temperature-stable coatings are preferably on the side of the glass ceramic plate that is not used and thus make it possible to provide color designs and to avoid the disruptive view of the technical elements below the transparent glass ceramic plate.
  • the cooking zones of the glass ceramic plate can be electrically radiant-heated, inductively heated or gas-heated.
  • the coating also to avoid the shielding action caused by the radiating heating elements.
  • radiant heating moreover, it is desirable that the bottom coating be infrared-transparent to ensure short boiling times.
  • the bottom coating can be designed differently in the hot areas and in the colder areas of the glass ceramic plate.
  • the top of the glass ceramic plate which also represents the side that is used during use as a cooking surface, can be decorated with decorative paints in the usual way.
  • the decorative embodiments can be designed to be expansive or compact and have various degrees of surface coatings.
  • the top decoration can also be designed such that together with the colored bottom coating, it produces certain impressions or designs.
  • the transparent glass ceramic plate contains a bottom coating with partial recesses. Indicators, displays, etc., can be attached under these recesses, which can be detected by the recess through the glass ceramic plate. Because of the low inherent colors according to the invention, the display indicators and screens have high color fidelity.
  • the light gray shade of the glass ceramic plate according to the invention is very advantageously produced in the displays compared to the brownish-yellow inherent color without Nd 2 O 3 content.
  • the glass ceramic plate according to the invention is especially suitable for color LED or LCD displays, and future color displays, screens and even televisions.
  • the high light transmission is also advantageous here. In this way, new functions, such as, e.g., showing cooking recipes or interactive functions (Internet, integration with other household appliances) or touch-screen control electronics can be integrated advantageously under the transparent, color-free glass ceramic plate.
  • the glasses of Table 1 were melted and plained with use of raw materials that are common in the glass industry at temperatures of about 1620° C.
  • the batch was melted in crucibles that consist of sintered silica glass and then poured into the Pt/Rh crucibles with inside crucibles made of silica glass and homogenized at temperatures of about 1550° C. for 30 minutes while being stirred.
  • castings of about 140 ⁇ 100 ⁇ 30 mm in size were poured and depressurized in an annealing furnace at about 660° C. and cooled to room temperature.
  • Test patterns for the measurement of the properties in the vitreous state and the plates for the glazing were prepared from the castings.
  • the Fe 2 O 3 contents produced by raw material contaminants are also cited in the compositions.
  • the water content of the glasses is 0.03-0.05 mol/l, corresponding to ⁇ OH values of 0.32 to 0.53 mm ⁇ 1 .
  • Table 1 shows the compositions of the starting glasses Nos. 1 to 8 according to the invention and the starting glasses 9 to 10 according to the prior art for comparison.
  • the starting glass 10 corresponds to a composition without Nd additive that is optimized relative to inherent color. This optimization is at the expense of a higher processing temperature V A and strong negative thermal expansion ⁇ 20/700 of the glass ceramic. Variegation of colors and Yellowness Index are comparatively higher values.
  • the properties in the vitreous state such as, e.g., transformation temperature Tg, processing temperature V A , upper devitrification limit OEG, thermal expansion between room temperature and 300° C., as well as the density are also cited.
  • the nucleating agent content is the upper devitrification limit below the processing temperature V A .
  • Glazing Program 1 (Total Time 147 Minutes):
  • Glazing Program 2 (Total Time 96 Minutes):
  • Tables 2 and 3 show the properties of the transparent glass ceramics with high-quartz mixed crystals as the prevailing crystal phase, which were produced with the glazing program 1 (Table 2) or 2 (Table 3). Examples 9 and 10 as well as 19 and 20 are comparison ceramics outside of the invention.
  • the transmission measurements were made on polished plates with a thickness of 4 mm and with standard illuminant C, 2°.
  • the color coordinates x and y in the CIE system are also cited.
  • the glass ceramics according to the invention confirm the advantageous action of the Nd feedstock and optionally in addition Co for reducing the disruptive inherent color (Yellowness Index, variegation of colors C*). High values of the light transmission (brightness) Y are also achieved.
  • the turbidity was measured with standard illuminant C on 3.6 mm-thick plates that are polished on both sides and with a commercial haze-guard plus measuring device of the BYK-Gardner Company and characterized by the haze value.
  • Transparent glass ceramic plates that are 4 mm thick with polished surfaces were provided with a coating that consists of a high-temperature-stable silver-metallic-colored luster paint according to the prior art (DE 10014373 C2).
  • the coating was baked on in an additional temperature treatment at 800° C.
  • the color of the coating was directly measured with a measuring device of the Datacolor Company, designation Mercury 2000, in remission (incident light) with standard illuminant C, 2°.
  • the measurements were now performed with this device, such that the color of the coating through the transparent glass ceramic plate was determined.
  • the disruptive influence of the inherent color of the transparent glass ceramic plate is produced during the measurement by altering the L*, a*, and b* values compared to the values measured directly on the coating.
  • the measurements (Tables 2 and 3) confirm the advantageous action of the color-free, transparent glass ceramic plates according to the invention.
  • the glazing program 1 in addition property values of the glass ceramics, such as infrared transmission at 1600 nm, thermal expansion between 20 and 700° C., density and the phase content of the main crystal phase that is measured with x-ray diffraction, that consist of high-quartz mixed crystals, as well as the mean crystallite size, are also indicated.
  • FIG. 1 shows the transmission spectra of the glass ceramic of Example 8 according to the invention and the comparison glass ceramic of Example 9.
  • the comparison example shows the disruptive coloring associated with a high Yellowness Index and chromaticity.
  • the glass ceramic according to the invention shows the characteristic absorption bands of the Nd ion, which are extremely well suited also for labeling the glass ceramic plates according to the invention. Moreover, they also simplify the recycling of the glass ceramic by optical cullet separation processes based on the absorption bands and the infrared fluorescence of the Nd ion.
  • FIG. 2 shows the color coordinates of the glass ceramics according to the invention, Examples 11 to 18, and the comparison glass ceramics, Examples 19 and 20, in the CIELAB system.
  • TABLE 1 Compositions and Properties of Starting Glasses According to the Invention and Comparison Glasses 9 and 10 Compositions in % by Weight Based Glass No.
US11/688,099 2006-03-20 2007-03-19 Transparent glass ceramic plate that has an opaque, colored bottom coating over the entire surface or over part of the surface Abandoned US20070232476A1 (en)

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US12/540,881 US7981823B2 (en) 2006-03-20 2009-08-13 Transparent glass ceramic plate that has an opaque, colored bottom coating over the entire surface or over part of the surface

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Application Number Priority Date Filing Date Title
EP06005598A EP1837314B1 (de) 2006-03-20 2006-03-20 Transparente, farblose Lithium-Aluminosilikat-Glaskeramikplatte mit blickdichter, farbiger Unterseitenbeschichtung
EP06005598.5 2006-03-20

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DE502006004506D1 (de) 2009-09-24
JP5352058B2 (ja) 2013-11-27
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US20100130342A1 (en) 2010-05-27
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