KR101657922B1 - - - glass-ceramic of lithium aluminosilicate type containing a solid solution of -spodumene - Google Patents
- - glass-ceramic of lithium aluminosilicate type containing a solid solution of -spodumene Download PDFInfo
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- KR101657922B1 KR101657922B1 KR1020157022878A KR20157022878A KR101657922B1 KR 101657922 B1 KR101657922 B1 KR 101657922B1 KR 1020157022878 A KR1020157022878 A KR 1020157022878A KR 20157022878 A KR20157022878 A KR 20157022878A KR 101657922 B1 KR101657922 B1 KR 101657922B1
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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
- 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
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B32/00—Thermal after-treatment of glass products not provided for in groups C03B19/00, C03B25/00 - C03B31/00 or C03B37/00, e.g. crystallisation, eliminating gas inclusions or other impurities; Hot-pressing vitrified, non-porous, shaped glass products
- C03B32/02—Thermal crystallisation, e.g. for crystallising glass bodies into glass-ceramic articles
-
- 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
-
- 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
- C03C4/02—Compositions for glass with special properties for coloured glass
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F24—HEATING; RANGES; VENTILATING
- F24C—DOMESTIC STOVES OR RANGES ; DETAILS OF DOMESTIC STOVES OR RANGES, OF GENERAL APPLICATION
- F24C15/00—Details
- F24C15/10—Tops, e.g. hot plates; Rings
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- H—ELECTRICITY
- H05—ELECTRIC TECHNIQUES NOT OTHERWISE PROVIDED FOR
- H05B—ELECTRIC HEATING; ELECTRIC LIGHT SOURCES NOT OTHERWISE PROVIDED FOR; CIRCUIT ARRANGEMENTS FOR ELECTRIC LIGHT SOURCES, IN GENERAL
- H05B3/00—Ohmic-resistance heating
- H05B3/68—Heating arrangements specially adapted for cooking plates or analogous hot-plates
- H05B3/74—Non-metallic plates, e.g. vitroceramic, ceramic or glassceramic hobs, also including power or control circuits
-
- 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
- C03C2204/00—Glasses, glazes or enamels with special properties
Abstract
The subject of the present invention is a glass-ceramics of the lithium aluminosilicate type containing the solid solution of? -Spodemine, for a thickness of 4 mm; The optical transmittance to 625 nm wavelength is in excess of 3.0%, in particular more than 3.5%, the optical transmittance to 950 nm wavelength is in the range of 50 to 50% L *, a *, b * color coordinates in the standard observer of 2 ° are in the range of 15.0 < L * Wherein the chemical composition comprises the following components within the defined weight limits: SnO 2 < RTI ID = 0.0 > 0.2% to 0.6%, in particular 0.25% to 0.5%, V 2 O 5 0.015% to 0.070%, in particular 0.015% to 0.050%, Cr 2 O 3 0.01% to 0.04% or Bi 2 O 3 0.05% to 3.0%, Fe 2 O 3 0.05% to <0.15%, As 2 O 3 + Sb 2 O 3 <0.1%, especially <0.05%.
Description
The present invention relates to the field of glass-ceramics. More particularly, the present invention relates to glass-ceramics which exhibit a specific appearance upon reflection as well as a controlled transmittance curve, and also articles made of such glass-ceramics, in particular cooktops, and such glass-ceramic precursor glasses.
For applications such as cooktops, and especially in heating systems with a copying system, the cooktop needs to meet certain requirements associated with its optical properties in both the visible and infrared regions. It is particularly important that the heating element can be concealed when not in operation, but can be clearly seen during operation. Energy efficiency of the device is also important to shorten the cooking time as much as possible. In particular, when the cooktop is fully integrated within the kitchen, the aesthetic appearance of the cooktop must also be considered. The most common glass-ceramic cooktops available on the market, such as those described in U.S. Patent No. 5,070,045, are glass-ceramics of the type of lithium aluminosilicate which comprise a crystal phase consisting essentially of the solid solution of? -Quartz, It has a very low light transmittance and a black appearance that matches most kitchens. To further improve such integration, it would be advantageous to have a cooktop that exhibits a different appearance. In particular, the gray top cooktop will be very nice.
It has been found that the use of clear glass-ceramics containing a solid solution of beta -quartz as the main crystal phase is not suitable for obtaining such an optical appearance, which makes them very low in transmittance (as defined by this application) This is because whatever the true color of transmission is, it always looks black, because it has.
One possible way to obtain such a color is to coat the surface of the clear glass-ceramic with, for example, a heat-resistant resin or a colored coating of enamel. However, in the case of the radiant heating system, there are few resins suitable for the high temperature reached by the cooktop. Also, attaching the resin or enamel involves an expensive additional step in the cooktop manufacturing process. Therefore, there is a need for a cooktop which is suitable for a radiant heating system and which exhibits desirable optical appearance without the need to add resin or enamel over the entire surface of the cooktop.
For this purpose, the subject matter of the present invention is a glass-ceramic of the lithium aluminosilicate type, primarily containing the solid solution of? -Spodumene, for a thickness of 4 mm;
- the light transmittance is in the range of 0.3 to 2%, in particular 0.6 to 1.7%
An optical transmittance of more than 2.0%, in particular more than 3.0%, at a wavelength of 625 nm,
Optical transmittance for a wavelength of 950 nm is in the range of 50 to 75%
- Optical transmittance to 1600 nm wavelength is more than 50%
L *, a *, b * color coordinates in a standard observer with a diffuse reflection for a light source D65 and 15 ° ≤ L * ≤ 40.0, -3.0 ≤ a * ≤ 3.0 and -10.0 ≤ b * ≤ 3.0
Glass-ceramic.
The glass-ceramics also have the following chemical composition within the defined weight limits:
SnO 2 0.2% to 0.6%, especially 0.25 to 0.5%
0.015 to 0.070% V 2 O 5 , especially 0.015 to 0.050%
0.01 to 0.04% Cr 2 O 3 or 0.05 to 3.0% Bi 2 O 3,
Fe 2 O 3 0.05 to <0.15%
As 2 O 3 + Sb 2 O 3 <0.1%, especially <0.05%
In the present specification, all the contents are expressed as% by weight.
The content of V 2 O 5 is preferably 0.060% or less.
The solid solution of β-spodumene preferably constitutes at least 20% by weight, especially 30% by weight or 40% by weight of the total crystalline fraction. Preferably, the glass-ceramics according to the invention comprise the solid solution of? -Spodermin as the main crystal phase. In some cases, the solid solution of β-spodumine may constitute more than 50%, especially 60%, more preferably 70% or 80% by weight of the total crystalline fraction. The glass-ceramics according to the invention may, in some cases, even contain the solid solution of beta -spodermin as the only crystal phase. In addition to the solid solution of β-spodumene, the free-ceramic may contain a solid solution of β-quartz. Thus, the crystalline fraction advantageously contains a solid solution of? -Spodemin and a solid solution of? -Quartz in a weight ratio of at least 20:80, especially 40:60, more particularly 50:50, even 60:40 or 70:30 As a mixture. In some cases, this ratio may be at least 80:20, 90:10, or 95: 5. The amount of a given crystalline phase can be determined by x-ray diffraction by the Rietveld method. The crystal fraction generally comprises at least 60% by weight, in particular 70% by weight, and even 75% by weight of the glass-ceramics.
The present inventors have developed a combination of such optical and chemical features, thereby achieving unique properties in terms of both aesthetic appearance (color that may be somewhat light gray to brownish) and functional properties. Various advantages of the present invention will become apparent as the description of the present invention proceeds.
The light transmittance (within the meaning of standard EN 410) for a 4 mm thickness is in the range of 0.3 to 2%, in particular 0.6 to 1.7%, more particularly 1.0 to 1.7%, more particularly 1.1 to 1.6%. At low light transmittance, the heating element (especially in the copying mode) is invisible during use, which causes safety problems. On the other hand, if the light transmittance is too high, even when the heating element is not in use, it causes a visual aesthetic problem.
The optical transmittance for a 625 nm wavelength is greater than 2.0%, especially greater than 3.0% or greater than 4.0%, preferably greater than 4.5% or even greater than 5.0%. The optical transmittance is generally 50% or less. As such, the red indicator typically used for the cooktop is fully visible through the glass-ceramic.
The optical transmittance for a wavelength of 950 nm is in the range of 50 to 75%, especially 55 to 70%, and it is possible to transmit and receive at such wavelengths so that a conventional electronic control key can be used.
The optical transmittance for a 1600 nm wavelength is in the range of at least 50%, especially 55% to 80%, more particularly 60% to 75%. This permeability affects the heating performance of the cooktop. If the permeability is too low, the heating performance is too low. If the permeability is too high, there is a risk of overheating.
The color obtained at the time of reflection corresponds to the diffuse reflection for the light source D65 and the L *, a *, b * color coordinates at a 2 ° standard observer according to the following inequality: 15.0 ≤ L * ≤ 40.0, -3.0 ≤ a * ≤ 3.0 And -10.0? B *? 3.0.
The color coordinates preferably satisfy at least one, more preferably two or three of the following inequalities:
- 20.0? L *? 30.0,
-1.5? A? 1.5,
- -5.0? B *? 1.0
Color coordinate is calculated by the first specular reflection and a base line obtained under the same measurement in a diffusion reflection spectrum by the normal incidence obtained by using an integrating sphere equipped with a spectral theory (Spectralon) ® spectrophotometer.
What the inventors have been able to prove after a long period of research is that the desired transmittance curve for the short reflectance and the desired color can be obtained by the presence of a very sophisticated content of colorant and clarifying agent which is surprisingly selected specifically with? will be. High values of L * demonstrate the importance of diffuse reflection due to the presence of β-spodumine crystals.
The composition comprises SnO 2 as a fining agent. Clarification is easier to perform and more efficient as the amount of SnO 2 present increases. However, it is desirable to minimize or even preferably avoid the de-glassification phenomenon and to control the effect of SnO 2 on optical transmittance and light reflection. This is because tin oxide can reduce the vanadium and iron present during the ceramization. The amount of SnO 2 required is 0.2 to 0.6% by weight, in particular 0.25 to 0.5% by weight, more particularly 0.4% by weight or less.
The glass-ceramics according to the present invention do not contain any of As 2 O 3 or Sb 2 O 3 , or contain only trace amounts of at least one of these toxic oxides, and SnO 2 replaces these conventional refining agents exist. When at least one of these compounds is present in minor amounts, it is present as a contaminant; This is due to the presence of cullet-type recycled materials (from previous glass-ceramics refined with these compounds) in the free nitridable starting material feed. In any case, only trace amounts of these toxic compounds may be present and As 2 O 3 + Sb 2 O 3 <1000 ppm, even less than 500 ppm.
V 2 O 5 is the main colorant of the glass-ceramics according to the invention. This is because V 2 O 5 significantly darkens the glass during the ceramization in the presence of SnO 2 (see above). V 2 O 5 absorbs mainly at less than 700 nm and can maintain a sufficiently high transmittance at 950 nm and in the infrared region in its presence. The amount of V 2 O 5 in the range of 0.015 to 0.070%, especially 0.015 to 0.060%, more particularly 0.015 to 0.050%, more particularly 0.015 to 0.035%, was found to be sufficient.
The present invention uses V 2 O 5 in combination with one or more other primary colorants selected from Cr 2 O 3 , Bi 2 O 3, and mixtures thereof.
According to one embodiment, the glass-ceramics include V 2 O 5 and Cr 2 O 3 (by the abovementioned amounts and contents described below), but not Bi 2 O 3 . Thus, the weight content of Cr 2 O 3 is in the range of 0.01 to 0.04%, especially 0.015 to 0.035%, more particularly 0.02 to 0.03%, and the Bi 2 O 3 content is zero.
According to another embodiment, the free-ceramic contains V 2 O 5 and Bi 2 O 3 (by the abovementioned content and contents described below), but not Cr 2 O 3 . Therefore, the weight content of Bi 2 O 3 is in the range of 0.05 to 3.0%, especially 0.1 to 2.0%, more particularly 0.2 or 0.3 to 1.0%, and the Cr 2 O 3 content is zero.
According to another embodiment, the glass-ceramics comprise V 2 O 5 , Bi 2 O 3 and Cr 2 O 3 (with the abovementioned contents and amounts mentioned below). In this case, the weight content of Cr 2 O 3 is preferably in the range of 0.01 to 0.03%, particularly 0.015 to 0.025%, and the weight content of Bi 2 O 3 is preferably 0.1 to 1%, especially 0.2 to 0.5% %.
Cr 2 O 3 , when present, is advantageously included in a weight content ranging from 0.015 to 0.035%, especially 0.02 to 0.03%. Bi 2 O 3 , when present, is advantageously included in a weight content ranging from 0.1 to 2.0%, especially 0.2 to 1.5%, more particularly 0.2 to 1.0%.
The glass-ceramics according to the invention generally have an optical transmittance of less than 0.1% for a wavelength of 450 nm.
Iron oxide absorbs mainly in the infrared region and its content should be at least 500 ppm, advantageously at least 700 ppm in order to obtain the required transmittance. If its content is at or above 1500 ppm, the glass-ceramic has a too high absorption rate in the infrared region and makes it more difficult to melt and purify in the starting glass. It is advantageous that the iron oxide has a weight content of 700 to 1200 ppm (0.07 to 0.12%).
The glass-ceramic contains at least some of the other colorants, such as CoO, CuO, MnO 2 , NiO or CeO 2 , in a considerable amount in addition to V 2 O 5 , Fe 2 O 3 , Bi 2 O 3 and Cr 2 O 3 Is not excluded from the scope of the present invention. Manganese oxide MnO 2 may be used to provide a brown bath. However, the presence of said at least one other coloring agent should not significantly affect the desired optical transmittance curve and the desired reflectivity appearance. In particular, it is desirable to watch the possibility of interacting with a low-content colorant to change the optical transmittance curve or the appearance at the time of reflection.
CoO can be present in very small quantities in the experience as long as this element absorbs strongly in the infrared region and absorbs little at 625 nm and imparts a blue color upon reflection. Preferably, the chemical composition of the free-ceramic comprises less than 200 ppm, advantageously 100 ppm, especially 50 ppm or 30 ppm cobalt oxide.
Likewise, the NiO content can preferably be zero except for up to 500 ppm, especially 200 ppm, even inevitable trace amounts. The CeO 2 content can preferably be zero, except for at most 0.5%, in particular 0.1%, even inevitable impurities. MnO 2 The content may preferably be at most 0.5%, in particular 0.1%, even zero, except for unavoidable impurities. The CuO content can preferably be zero, except for up to 500 ppm, especially 200 ppm, and even unavoidable impurities.
Preferably, the composition of the glass-ceramics according to the invention does not comprise a finishing aid such as F and Br. The composition of the glass-ceramics does not include F and Br except for trace amounts. This is particularly preferred in view of the price and / or toxicity of these compounds. In the compositions of the present invention, the presence of a finishing aid is not necessary as long as SnO 2 is present in the above amounts.
The base composition of the glass-ceramics of the present invention can be widely varied. Preferably, the chemical composition of the glass-ceramic contains the following ingredients within the defined weight limits:
SiO 2 60 to 72%
Al 2 O 3 18 to 23%
Li 2 O 2.5 to 4.5%
MgO 0 to 3%
1 to 3% of ZnO,
TiO 2 1.5 to 4%
ZrO 2 0 to 2.5%
BaO 0 to 5%
SrO 0 to 5%
At this time, BaO + SrO 0 to 5%
CaO 0 to 2%
Na 2 O 0 to 1.5%
K 2 O 0 to 1.5%
P 2 O 5 0 to 5%
B 2 O 3 0 to 2%
These compositions are themselves perfect for the melting of glass precursors and subsequent ceramicization, in particular the development of? -Spodumin solid solutions.
Preferably, the weight content of MgO is at most 2%, especially 1%. The weight content of CaO is advantageously at most 1%. The sum of the weight content of Na 2 O and K 2 O is preferably at most 1%, in particular 0.5%. The weight content of BaO is preferably at most 3%, especially 2%, even 1%. By using these different preferred ranges alone or in combination, the coefficient of thermal expansion of the glass-ceramics can be reduced.
Preferably, SiO 2 , Al 2 O 3 , Li 2 O, MgO, ZnO, TiO 2 , ZrO 2 , BaO, SrO, CaO, Na 2 O, Li 2 O, K 2 O, P 2 O 5 , B The sum of the contents of 2 O 3 , SnO 2 , V 2 O 5 , Fe 2 O 3 , Cr 2 O 3 and Bi 2 O 3 is at least 98%, in particular 99%.
Another subject of the invention is an article comprising glass-ceramics according to the invention. The article advantageously consists entirely of glass-ceramics according to the invention. The article is in particular a cooktop, cookware or microwave oven floor. It is advantageous for the cooktop to be included in a cooking device, in particular a radiative heating cooker comprising one or more elements that are heated by radiation. The cooktop can be coated with decorative enamel.
In particular, when the cooktop has an element that generates heat by radiation (radiation heating system), it is advantageous for the glass-ceramic to have a linear thermal expansion coefficient of between 10 and 10 <" 7 >
Another subject of the present invention is a lithium aluminosilicate glass which is a precursor of the glass-ceramics of the present invention as described above. The glass represents the bulk composition of the glass-ceramic as described above. It should also be appreciated that the precursor glass advantageously has an optical transmittance of greater than 60% at any wavelength between 1000 and 2500 nm for a thickness of 3 mm. In such a case, melting and refining are promoted.
Finally, the subject of the present invention is a process for the production of glass-ceramics according to the invention comprising heat-treating the glass-nitridable starting material feed under conditions which continuously provide melting, clarification and subsequent ceramization, Wherein the input represents a composition which enables the obtaining of the glass-ceramics according to the invention.
Ceramization is carried out at a temperature at which the solid solution of? -Spodermin can develop. Appropriate ceramization temperatures can be varied as a function of the free matrix and can be selected after differential thermal analysis, and by this thermal analysis, the crystallization temperature of the? -Sque image, and at higher temperatures, You can determine the temperature at which (irreversible) deformation to the dumin occurs. The ceramization temperature may preferably be at least 950 ° C, in particular 970 ° C, even 1000 ° C or 1020 ° C.
The following examples illustrate the invention without limiting it.
The different glasses given the chemical compositions (weight content of oxides) in the following Tables 1 and 2 were melted in a known manner.
Composition C1 (for comparison) did not contain any of Bi 2 O 3 and Cr 2 O 3 . Other compositions are in accordance with the present invention.
The glass plate was then ceramized according to different cycles, characterized by different ceramicization temperatures and steady state times at that temperature. The ceramicization cycle is followed by rapid heating to 650 ° C followed by heating to 820 ° C at a rate of 5 ° C / minute and finally heating to the ceramization temperature at a rate of 15 ° C / minute followed by maintenance at that temperature.
The obtained results are summarized in Tables 3 and 4, and the following items are shown:
- the type of glass used for the ceramics,
- Ceramic temperature, indicated by T (℃)
- steady state time at the ceramic temperature, indicated by t (min)
- the thickness of the plate, expressed in th (mm)
Transmittance characteristics at true thickness, calculated from transmission spectra recorded by a spectrophotometer: light transmittance in the sense of standard EN 410 (expressed in LT) and 625 nm (expressed in T625), 950 nm (indicated in T950) ) And a transmittance at a wavelength of 1600 nm (expressed as T1600)
- calculated by the the L * a * b * color coordinates, the regular reflection, and the baseline obtained from the same measurement in a diffusion reflection spectrum by the vertical incidence is obtained by the integrating sphere is used for the mounting spectral theory ® spectrophotometer in diffuse reflection,
- type of crystal: Q represents? -Quartz as the main crystal phase and S represents the presence of a considerable amount of? -Spodumin as the crystal phase.
Comparative Example A has advantageous transmission characteristics according to the requirements, but does not exhibit a very desirable appearance because it appears black during reflection. It crystallized essentially in the β-quartz form due to the too low ceramization temperature to grow β-spodumine crystals.
In order to cause the growth of β-spoduimin type crystals, the same glass was ceramicized at a higher temperature. In Examples B and C according to the present invention, the transmission characteristics were substantially maintained, Lt; RTI ID = 0.0 > L * < / RTI > value. The sample exhibited the desired coloration.
In the case of Comparative Example D, the glass-ceramics which were comparatively ceramized for the comparative composition C1 to cause the growth of? -Spodylminic crystals showed a blue color on reflection, on the other hand, B * and an excessively high a * value.
Compared with Examples B and C, Example E exhibited a lower light transmittance and a brighter hue than reflected at the same time. Embodiments F to K are other embodiments according to the present invention.
Claims (13)
- the light transmittance is in the range of 0.3 to 2%
An optical transmittance of more than 2.0% for a wavelength of 625 nm,
Optical transmittance for a wavelength of 950 nm is in the range of 50 to 75%
- Optical transmittance to 1600 nm wavelength is more than 50%
L *? 40.0, -3.0? A *? 3.0, and -10.0? B *? 3.0 in the diffuse reflection for the light source D65 and the L *, a *, b *
Wherein the chemical composition comprises the following components in the weight percentages defined below.
SnO 2 0.2% to 0.6%;
0.015 to 0.070% V 2 O 5 ;
0.01 to 0.04% Cr 2 O 3 or 0.05 to 3.0% Bi 2 O 3 ;
0.05 to < 0.15% Fe 2 O 3 ;
As 2 O 3 + Sb 2 O 3 <0.1%
SiO 2 60 to 72%
Al 2 O 3 18 to 23%
Li 2 O 2.5 to 4.5%
MgO 0 to 3%
1 to 3% of ZnO,
TiO 2 1.5 to 4%
ZrO 2 0 to 2.5%
BaO 0 to 5%
SrO 0 to 5%
At this time, BaO + SrO 0 to 5%
CaO 0 to 2%
Na 2 O 0 to 1.5%
K 2 O 0 to 1.5%
P 2 O 5 0 to 5%
B 2 O 3 0 to 2%
Applications Claiming Priority (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| FR1351769 | 2013-02-28 | ||
| US201361803577P | 2013-03-20 | 2013-03-20 | |
| US61/803,577 | 2013-03-20 | ||
| PCT/FR2013/051769 WO2014016507A1 (en) | 2012-07-23 | 2013-07-23 | Novel selective compounds inhibiting cyp26a1 useful in cosmetic and pharmaceutical compositions |
| PCT/FR2014/050438 WO2014132005A1 (en) | 2013-02-28 | 2014-02-28 | Glass-ceramic of lithium aluminosilicate type containing a solid solution of β-spodumene |
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| KR20150123240A KR20150123240A (en) | 2015-11-03 |
| KR101657922B1 true KR101657922B1 (en) | 2016-09-19 |
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| DE202018100558U1 (en) * | 2017-08-30 | 2018-02-15 | Schott Ag | Colored transparent lithium aluminum silicate glass-ceramic |
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| WO2012016724A1 (en) | 2010-08-03 | 2012-02-09 | Eurokera | LITHIUM ALUMINOSILICATE GLASSES; GLASS-CERAMICS OF β-QUARTZ AND/OR β-SPODUMENE; ARTICLES IN SAID GLASSES AND GLASS-CERAMICS; METHODS FOR OBTAINING THE SAME |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| WO2012016724A1 (en) | 2010-08-03 | 2012-02-09 | Eurokera | LITHIUM ALUMINOSILICATE GLASSES; GLASS-CERAMICS OF β-QUARTZ AND/OR β-SPODUMENE; ARTICLES IN SAID GLASSES AND GLASS-CERAMICS; METHODS FOR OBTAINING THE SAME |
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