CA2178033C - Glazing panel having solar screening properties and a process for making such a panel - Google Patents
Glazing panel having solar screening properties and a process for making such a panel Download PDFInfo
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- CA2178033C CA2178033C CA002178033A CA2178033A CA2178033C CA 2178033 C CA2178033 C CA 2178033C CA 002178033 A CA002178033 A CA 002178033A CA 2178033 A CA2178033 A CA 2178033A CA 2178033 C CA2178033 C CA 2178033C
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- coating layer
- glazing panel
- panel according
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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
- C03C17/00—Surface treatment of glass, not in the form of fibres or filaments, by coating
- C03C17/22—Surface treatment of glass, not in the form of fibres or filaments, by coating with other inorganic material
- C03C17/23—Oxides
- C03C17/25—Oxides by deposition from the liquid phase
- C03C17/253—Coating containing SnO2
-
- 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
- C03C17/00—Surface treatment of glass, not in the form of fibres or filaments, by coating
- C03C17/34—Surface treatment of glass, not in the form of fibres or filaments, by coating with at least two coatings having different compositions
- C03C17/3411—Surface treatment of glass, not in the form of fibres or filaments, by coating with at least two coatings having different compositions with at least two coatings of inorganic materials
- C03C17/3417—Surface treatment of glass, not in the form of fibres or filaments, by coating with at least two coatings having different compositions with at least two coatings of inorganic materials all coatings being oxide coatings
-
- 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
- C03C17/00—Surface treatment of glass, not in the form of fibres or filaments, by coating
- C03C17/34—Surface treatment of glass, not in the form of fibres or filaments, by coating with at least two coatings having different compositions
- C03C17/3411—Surface treatment of glass, not in the form of fibres or filaments, by coating with at least two coatings having different compositions with at least two coatings of inorganic materials
- C03C17/3423—Surface treatment of glass, not in the form of fibres or filaments, by coating with at least two coatings having different compositions with at least two coatings of inorganic materials at least one of the coatings comprising a suboxide
-
- 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
- C03C2217/00—Coatings on glass
- C03C2217/20—Materials for coating a single layer on glass
- C03C2217/21—Oxides
- C03C2217/211—SnO2
-
- 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
- C03C2217/00—Coatings on glass
- C03C2217/20—Materials for coating a single layer on glass
- C03C2217/21—Oxides
- C03C2217/24—Doped oxides
- C03C2217/244—Doped oxides with Sb
-
- 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
- C03C2218/00—Methods for coating glass
- C03C2218/10—Deposition methods
- C03C2218/11—Deposition methods from solutions or suspensions
- C03C2218/112—Deposition methods from solutions or suspensions by spraying
-
- 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
- C03C2218/00—Methods for coating glass
- C03C2218/10—Deposition methods
- C03C2218/15—Deposition methods from the vapour phase
- C03C2218/152—Deposition methods from the vapour phase by cvd
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- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Engineering & Computer Science (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General Chemical & Material Sciences (AREA)
- Geochemistry & Mineralogy (AREA)
- Life Sciences & Earth Sciences (AREA)
- Organic Chemistry (AREA)
- Surface Treatment Of Glass (AREA)
- Laminated Bodies (AREA)
- Physical Vapour Deposition (AREA)
- Joining Of Glass To Other Materials (AREA)
- Glass Compositions (AREA)
- Special Wing (AREA)
Abstract
A glazing panel having solar screening properties and a process for making such a panel. A glazing panel comprises a vitreous substrate carrying a pyrolytically formed tin/antimony oxide coating layer containing tin and antimony in a Sb/Sn molar ratio of from 0.01 to 0.5. The coated substrate has a solar factor FS of less than 70%. The panel is formed by chemical vapour deposition from a reactant mixture comprising a source of tin and a source of antimony.
Description
- ~.
A glazing panel having solar screening properties and a process for making such a panel.
The present invention relates to a glazing panel having solar screening properties and to a process for making such a panel.
Reflective transparent solar control glazing panels have become a useful material for architects to use for the exterior facade of buildings.Such panels have aesthetic qualities in reflecting the immediate environment and, being available in a number of colours, in providing a design opportunity. Such panels also have technical advantages by providing the occupants of a building with protection against solar radiation by reflection and/or absorption and eliminating the dazzling effects of intense sunshine, giving an effective screen against glare, enhancing visual comfort and reducing eye fatigue.
From a technical point of view, it is desired that the glazing panel shall not pass too great a proportion of total incident solar radiation in order that the interior of the building shall not become overheated in sunny weather. The transmission of total incident solar radiation may be expressed in terms of the "solar factor". As used herein, the term "solar factor" means the sum of the total energy directly transmitted and the energy which is absorbed and re-radiated on the side away from the energy source, as a proportion of the total radiant energy incident of the coated glass.
Another important application of reflective transparent solar control glazing panels is in vehicle windows, especially for motor cars or railway carriages, where the objective is to protect the vehicle occupants against solar radiation. In this case the main energy factor to be considered is the total energy directly transmitted (TE), since the energy which is internally absorbed and re-radiated (AE) is dissipated by the movement of the vehicle. The essential aim of the vehicle panel is thus to have a low TE factor.
The properties of the coated substrate discussed herein are based on the standard definitions of the International Commission on Illumination -Commission Internationale de 1 E'clairaye ("CIE").
The standard illuminants quoted herein are CIE Illuminant C and Illuminant A. Illuminant C represents average daylight having a colour temperature of 6700 K. Illuminant A represents the radiation of a Planck radiator at a temperature of about 2856 K.
The "luminous transmittance" (TL) is the luminous flux transmitted 2.
through a substrate as a percentage of the incident luminous flux.
The "luminous reflectance" (RL) is the luminous flux reflected from a substrate as a percentage of the incident luminous flux.
The "selectivity" of a coated substrate for use in a building glazing panel is the ratio of the luminous transmittance to the solar factor (TUFS).
The " purity" (p) of the colour of the substrate refers to the excitation purity measured with Iltuminant C. It is specified according to a linear scale on which a defined white light source has a purity of zero and the pure colour has a purity of 100%. The purity of the coated substrate is measured from the side opposite the coated side.
The term "refractive index" (n) is defined in the CIE International Lighting Vocabulary, 1987, page 138.
The "dominant wavelength" RD) is the peak wavelength in the range transmitted or reflected by the coated substrate.
The "emissivity" (e) is the ratio of the energy emitted by a given surface at a given temperature to that of a perfect emitter (black body with emissivity of 1.0) at the same temperature.
A number of techniques are known for forming coatings on a vitreous substrate, including pyrolysis. Pyrolysis generally has the advantage of producing a hard coating, which precludes the need for a protective layer. The coatings formed by pyrolysis have durable abrasive- and corrosion-resistant properties. It is believed that this is due in particular to the fact the process involves depositing of coating material onto a substrate which is hot. Pyrolysis is also generally cheaper than alternative coating processes such as sputtering, particularly in terms of the investment in plant.
The deposit of coatings by other processes, for example by sputtering, led to products with very different properties, in particular a lower resistance to abrasion and occasionatly a different refractive index.
A wide variety of coating materials have been proposed for glazing panels, and for several different desired properties of the glazing. Tin oxide, SnO2, has been widely used, often in combination with other materials such as other metal oxides.
GB patent 1455148 teaches a method for pyrolytically forming a coating of one or more oxides on a substrate, primarily by spraying compounds of a metal or silicon, so as to modify the light transmission and/or light reflection of the substrate, or to impart antistatic or electrically conductive properties. Its examples of specified oxides include Zr02, SnO2, Sb203, Ti02, Co304, Cr203, Si02 and mixtures thereof. Tin oxide (SnO2) is seen as advantageous because of its hardness and its abitity to have antistatic or electrically conductive properties. GB patent 3.
relates to a sequential spray method for pyrolytically forming a coating on a vitreous support and is particularly concerned with tin oxide or indium oxide as the main coating constituents. When its metal coating precursor is tin chloride this is advantageously doped with a precursor selected from ammonium bifluoride and antimony chloride in order to increase the electrical conductivity of the coating.
It is also known that where a coating of tin oxide is formed by pyrolysis of SnC4, the presence of a dopant such as antimony chloride SbC15, directly mixed with the tin chloride SnC4, improves the absorption and reflection of some near solar infrared radiation.
It is an object of the present invention to provide a pyrolytically formed glazing panel having solar screening properties.
We have discovered that this and other useful objectives can be achieved by utilising chemical vapour deposition (CVD) to apply a pyrolytic coating comprising tin and antimony oxides in a specific relative ratio.
Thus, according to a first aspect of the present invention, there is provided a glazing panel comprising a vitreous substrate carrying a tin/antimony oxide coating layer containing tin and antimony in a Sb/Sn molar ratio of from 0.01 to 0.5, the said coating layer having been pyrolytically formed by chemical vapour deposition, whereby the so-coated substrate has a solar factor FS of less than 70%.
The substrate is preferably in the form of a ribbon of vitreous material, such as glass or some other transparent rigid material. In view of the proportion of incident solar radiation which is absorbed by the glazing panel, especially in environments where the panel is exposed to strong or long-term solar radiation, there is a heating effect on the glass panel which may require that the glass substrate be subsequently subjected to a toughening process. However, the durability of the coating enables the glazing panel to be mounted with the coated face outermost, thus reducing the heating effect.
Preferably, the substrate is clear glass, although the invention also extends to the use of coloured glass as the substrate.
The Sb/Sn molar ratio in the coating layer is preferably at least 0.03, most preferably at least 0.05. This assists in ensuring a high level of absorption. On the other hand the said ratio is preferably less than 0.21, with a view to achieving a high level of luminous transmittance (TL). Most preferably the ratio is less than 0.15, since above this level the coating layer displays an unduly high level of absorption, coupled with poor selectivity.
Coated substrates according to the invention offer the advantage of a luminous reflectance (RL) of less than 11%. This low level of reflection in a building glazing panel is much favoured by architects. It avoids the panels creating glare in the 4.
vicinity of the building.
It may be useful to prevent interaction between the glass of the substrate and the tin/antimony oxide coating layer. As an example, it has been found that in the pyrolytic formation of a tin oxide coating from tin chloride on a soda-lime glass substrate, sodium chloride tends to become incorporated into the coating as a result of reaction of the glass with the coating precursor material or its reaction products, and this leads to haze in the coating.
Thus, an intermediate haze-reducing coating layer is preferably positioned between the substrate and the tin/antimony oxide coating layer. The haze-reducing layer may be pyrolytically formed in an incompletely oxidized state by contacting the substrate in an undercoating chamber with undercoat precursor material in the presence of oxygen in insufficient quantity for full oxidation of the undercoat material on the substrate. The expression "incompletely oxidized material"
is used herein to denote a true sub-oxide, that it to say an oxide of a lower valency state of a multivalent element (for example V02 or TiO), and also to denote an oxide material which contains oxygen gaps in its structure: an example of the latter material is SiOx where x is less than 2, which may have the general structure of Si02 but has a proportion of gaps which would be filled with oxygen in the dioxide.
We prefer the haze-reducing coating layer to comprise a silicon oxide having a geometric thickness such as about 100 nm. The presence of a silicon oxide undercoating on soda-lime glass has the particular benefit of inhibiting the migration of sodium ions from the glass whether by diffusion or otherwise into the tin/antimony oxide coating layer either during formation of that upper layer or during a subsequent high temperature treatment.
Alternatively, the undercoat may be constituted as an "anti-reflection"
undercoating such as, for example, an oxidised aluminium/vanadium layer as described in GB patent specification 2248243.
The glazing panels according to the invention have a solar factor of less than 70%, preferably less than 60% and in some instances preferably less than 50%.
The preference for a solar factor of less than 60% arises when the panels according to the invention are positioned with the coated side facing the exterior, i.e.
facing the energy source. Generally, this positioning leads to a improved solar factor compared with the positioning of the panel with the coated side away from the energy source.
The need for a solar factor of less than 50% arises for buildings in parts of the world with high levels of solar energy. For vehicle sunroofs an even lower solar factor may be desirable.
The use of coloured glass is one way of providing a lower solar factor, and is commonly employed in both building glass and vehicle glass. In comparing the 5.
effectiveness of coating layers it is therefore necessary to take into account any differences between the types of glass on which the respective coatings are deposited.
Thus one example of a coating according to the invention on clear glass gave a solar factor of 63%, whereas an equivalent coating on a green coloured glass gave a solar factor of 44.5%.
It is also desired that the glazing panel shall also transmit a reasonable proportion of visible light in order to allow natural illumination of the interior of the building or vehicle and in order to allow its occupants to see out. Thus it is desirable to increase the selectivity of the coating, that is to increase the ratio of the transmittance to the solar factor. Indeed it is preferred that the selectivity be as high as possible.
In general it is preferred that the luminous transmittance (TL) of the panel according to the invention is between 40 and 65%. Nevertheless, a panel having a light transmittance below 40% may be used as a roofing panel, for example as a vehicle sunroof.
Preferably, the tin/antimony oxide coating has a thickness of from 100 to 500 nm. Thick layers of tin/antimony oxide, particularly layers having a low Sb/Sn molar ratio, can provide a glazing panel with the advantageous combination of a low solar factor (FS) and low emissivity. Another way of obtaining this combination is to deposit on the tin/antimony oxide layer of the invention a low-emissivity layer of doped tin oxide, for example tin oxide doped with fluorine. However this is disadvantageous in the sense that it makes necessary the deposition of a supplementary layer, which is time-consuming and expensive.
In principle, another way to provide a combination of low solar factor and low emissivity could be to form a tin/antimony oxide layer containing a doping agent such as fluorine. For example GB patent 2200139 teaches a method of forming a pyrolytic tin oxide coating by spraying a solution which in addition to the tin precursor contains compounds which will result in the coating containing fluorine and at least one of antimony, arsenic, vanadium, cobalt, zinc, cadmium, tungsten, te(lurium and manganese.
Thus one could, for instance, form a coating from reactants containing tin, antimony and fluorine in the ratios Sb/Sn = 0.028, F/Sn = 0.04. However we have discovered that the presence of fluorine has the apparent disadvantage of hindering the incorporation of antimony in the coating rather than effectively reducing the emissivity. For example reactants containing antimony and tin in the ratio Sb/Sn = 0.028 gave a coating with an Sb/Sn ratio of about 0.057, whilst the same reactants plus a fluorine-containing reactant in an amount such that F/Sn =
0.04 gave a coating with an Sb/Sn ratio of about 0.038.
A glazing panel having solar screening properties and a process for making such a panel.
The present invention relates to a glazing panel having solar screening properties and to a process for making such a panel.
Reflective transparent solar control glazing panels have become a useful material for architects to use for the exterior facade of buildings.Such panels have aesthetic qualities in reflecting the immediate environment and, being available in a number of colours, in providing a design opportunity. Such panels also have technical advantages by providing the occupants of a building with protection against solar radiation by reflection and/or absorption and eliminating the dazzling effects of intense sunshine, giving an effective screen against glare, enhancing visual comfort and reducing eye fatigue.
From a technical point of view, it is desired that the glazing panel shall not pass too great a proportion of total incident solar radiation in order that the interior of the building shall not become overheated in sunny weather. The transmission of total incident solar radiation may be expressed in terms of the "solar factor". As used herein, the term "solar factor" means the sum of the total energy directly transmitted and the energy which is absorbed and re-radiated on the side away from the energy source, as a proportion of the total radiant energy incident of the coated glass.
Another important application of reflective transparent solar control glazing panels is in vehicle windows, especially for motor cars or railway carriages, where the objective is to protect the vehicle occupants against solar radiation. In this case the main energy factor to be considered is the total energy directly transmitted (TE), since the energy which is internally absorbed and re-radiated (AE) is dissipated by the movement of the vehicle. The essential aim of the vehicle panel is thus to have a low TE factor.
The properties of the coated substrate discussed herein are based on the standard definitions of the International Commission on Illumination -Commission Internationale de 1 E'clairaye ("CIE").
The standard illuminants quoted herein are CIE Illuminant C and Illuminant A. Illuminant C represents average daylight having a colour temperature of 6700 K. Illuminant A represents the radiation of a Planck radiator at a temperature of about 2856 K.
The "luminous transmittance" (TL) is the luminous flux transmitted 2.
through a substrate as a percentage of the incident luminous flux.
The "luminous reflectance" (RL) is the luminous flux reflected from a substrate as a percentage of the incident luminous flux.
The "selectivity" of a coated substrate for use in a building glazing panel is the ratio of the luminous transmittance to the solar factor (TUFS).
The " purity" (p) of the colour of the substrate refers to the excitation purity measured with Iltuminant C. It is specified according to a linear scale on which a defined white light source has a purity of zero and the pure colour has a purity of 100%. The purity of the coated substrate is measured from the side opposite the coated side.
The term "refractive index" (n) is defined in the CIE International Lighting Vocabulary, 1987, page 138.
The "dominant wavelength" RD) is the peak wavelength in the range transmitted or reflected by the coated substrate.
The "emissivity" (e) is the ratio of the energy emitted by a given surface at a given temperature to that of a perfect emitter (black body with emissivity of 1.0) at the same temperature.
A number of techniques are known for forming coatings on a vitreous substrate, including pyrolysis. Pyrolysis generally has the advantage of producing a hard coating, which precludes the need for a protective layer. The coatings formed by pyrolysis have durable abrasive- and corrosion-resistant properties. It is believed that this is due in particular to the fact the process involves depositing of coating material onto a substrate which is hot. Pyrolysis is also generally cheaper than alternative coating processes such as sputtering, particularly in terms of the investment in plant.
The deposit of coatings by other processes, for example by sputtering, led to products with very different properties, in particular a lower resistance to abrasion and occasionatly a different refractive index.
A wide variety of coating materials have been proposed for glazing panels, and for several different desired properties of the glazing. Tin oxide, SnO2, has been widely used, often in combination with other materials such as other metal oxides.
GB patent 1455148 teaches a method for pyrolytically forming a coating of one or more oxides on a substrate, primarily by spraying compounds of a metal or silicon, so as to modify the light transmission and/or light reflection of the substrate, or to impart antistatic or electrically conductive properties. Its examples of specified oxides include Zr02, SnO2, Sb203, Ti02, Co304, Cr203, Si02 and mixtures thereof. Tin oxide (SnO2) is seen as advantageous because of its hardness and its abitity to have antistatic or electrically conductive properties. GB patent 3.
relates to a sequential spray method for pyrolytically forming a coating on a vitreous support and is particularly concerned with tin oxide or indium oxide as the main coating constituents. When its metal coating precursor is tin chloride this is advantageously doped with a precursor selected from ammonium bifluoride and antimony chloride in order to increase the electrical conductivity of the coating.
It is also known that where a coating of tin oxide is formed by pyrolysis of SnC4, the presence of a dopant such as antimony chloride SbC15, directly mixed with the tin chloride SnC4, improves the absorption and reflection of some near solar infrared radiation.
It is an object of the present invention to provide a pyrolytically formed glazing panel having solar screening properties.
We have discovered that this and other useful objectives can be achieved by utilising chemical vapour deposition (CVD) to apply a pyrolytic coating comprising tin and antimony oxides in a specific relative ratio.
Thus, according to a first aspect of the present invention, there is provided a glazing panel comprising a vitreous substrate carrying a tin/antimony oxide coating layer containing tin and antimony in a Sb/Sn molar ratio of from 0.01 to 0.5, the said coating layer having been pyrolytically formed by chemical vapour deposition, whereby the so-coated substrate has a solar factor FS of less than 70%.
The substrate is preferably in the form of a ribbon of vitreous material, such as glass or some other transparent rigid material. In view of the proportion of incident solar radiation which is absorbed by the glazing panel, especially in environments where the panel is exposed to strong or long-term solar radiation, there is a heating effect on the glass panel which may require that the glass substrate be subsequently subjected to a toughening process. However, the durability of the coating enables the glazing panel to be mounted with the coated face outermost, thus reducing the heating effect.
Preferably, the substrate is clear glass, although the invention also extends to the use of coloured glass as the substrate.
The Sb/Sn molar ratio in the coating layer is preferably at least 0.03, most preferably at least 0.05. This assists in ensuring a high level of absorption. On the other hand the said ratio is preferably less than 0.21, with a view to achieving a high level of luminous transmittance (TL). Most preferably the ratio is less than 0.15, since above this level the coating layer displays an unduly high level of absorption, coupled with poor selectivity.
Coated substrates according to the invention offer the advantage of a luminous reflectance (RL) of less than 11%. This low level of reflection in a building glazing panel is much favoured by architects. It avoids the panels creating glare in the 4.
vicinity of the building.
It may be useful to prevent interaction between the glass of the substrate and the tin/antimony oxide coating layer. As an example, it has been found that in the pyrolytic formation of a tin oxide coating from tin chloride on a soda-lime glass substrate, sodium chloride tends to become incorporated into the coating as a result of reaction of the glass with the coating precursor material or its reaction products, and this leads to haze in the coating.
Thus, an intermediate haze-reducing coating layer is preferably positioned between the substrate and the tin/antimony oxide coating layer. The haze-reducing layer may be pyrolytically formed in an incompletely oxidized state by contacting the substrate in an undercoating chamber with undercoat precursor material in the presence of oxygen in insufficient quantity for full oxidation of the undercoat material on the substrate. The expression "incompletely oxidized material"
is used herein to denote a true sub-oxide, that it to say an oxide of a lower valency state of a multivalent element (for example V02 or TiO), and also to denote an oxide material which contains oxygen gaps in its structure: an example of the latter material is SiOx where x is less than 2, which may have the general structure of Si02 but has a proportion of gaps which would be filled with oxygen in the dioxide.
We prefer the haze-reducing coating layer to comprise a silicon oxide having a geometric thickness such as about 100 nm. The presence of a silicon oxide undercoating on soda-lime glass has the particular benefit of inhibiting the migration of sodium ions from the glass whether by diffusion or otherwise into the tin/antimony oxide coating layer either during formation of that upper layer or during a subsequent high temperature treatment.
Alternatively, the undercoat may be constituted as an "anti-reflection"
undercoating such as, for example, an oxidised aluminium/vanadium layer as described in GB patent specification 2248243.
The glazing panels according to the invention have a solar factor of less than 70%, preferably less than 60% and in some instances preferably less than 50%.
The preference for a solar factor of less than 60% arises when the panels according to the invention are positioned with the coated side facing the exterior, i.e.
facing the energy source. Generally, this positioning leads to a improved solar factor compared with the positioning of the panel with the coated side away from the energy source.
The need for a solar factor of less than 50% arises for buildings in parts of the world with high levels of solar energy. For vehicle sunroofs an even lower solar factor may be desirable.
The use of coloured glass is one way of providing a lower solar factor, and is commonly employed in both building glass and vehicle glass. In comparing the 5.
effectiveness of coating layers it is therefore necessary to take into account any differences between the types of glass on which the respective coatings are deposited.
Thus one example of a coating according to the invention on clear glass gave a solar factor of 63%, whereas an equivalent coating on a green coloured glass gave a solar factor of 44.5%.
It is also desired that the glazing panel shall also transmit a reasonable proportion of visible light in order to allow natural illumination of the interior of the building or vehicle and in order to allow its occupants to see out. Thus it is desirable to increase the selectivity of the coating, that is to increase the ratio of the transmittance to the solar factor. Indeed it is preferred that the selectivity be as high as possible.
In general it is preferred that the luminous transmittance (TL) of the panel according to the invention is between 40 and 65%. Nevertheless, a panel having a light transmittance below 40% may be used as a roofing panel, for example as a vehicle sunroof.
Preferably, the tin/antimony oxide coating has a thickness of from 100 to 500 nm. Thick layers of tin/antimony oxide, particularly layers having a low Sb/Sn molar ratio, can provide a glazing panel with the advantageous combination of a low solar factor (FS) and low emissivity. Another way of obtaining this combination is to deposit on the tin/antimony oxide layer of the invention a low-emissivity layer of doped tin oxide, for example tin oxide doped with fluorine. However this is disadvantageous in the sense that it makes necessary the deposition of a supplementary layer, which is time-consuming and expensive.
In principle, another way to provide a combination of low solar factor and low emissivity could be to form a tin/antimony oxide layer containing a doping agent such as fluorine. For example GB patent 2200139 teaches a method of forming a pyrolytic tin oxide coating by spraying a solution which in addition to the tin precursor contains compounds which will result in the coating containing fluorine and at least one of antimony, arsenic, vanadium, cobalt, zinc, cadmium, tungsten, te(lurium and manganese.
Thus one could, for instance, form a coating from reactants containing tin, antimony and fluorine in the ratios Sb/Sn = 0.028, F/Sn = 0.04. However we have discovered that the presence of fluorine has the apparent disadvantage of hindering the incorporation of antimony in the coating rather than effectively reducing the emissivity. For example reactants containing antimony and tin in the ratio Sb/Sn = 0.028 gave a coating with an Sb/Sn ratio of about 0.057, whilst the same reactants plus a fluorine-containing reactant in an amount such that F/Sn =
0.04 gave a coating with an Sb/Sn ratio of about 0.038.
6.
The invention accordingly presents the advantage of simultaneously providing a solar factor (FS) below 60%, an emissivity of less than 0.4 (preferably less than 0.3) and a luminous transmittance (TL) of more than 60%. Thus the coated product fulfil two important functions. In winter it maintains the heat in the building, because of its low emissivity. In summer it resists the passage of solar heat into the building and thus avoids overheating inside the building, thanks to its low solar factor.
This is especially achieved for coatings having an Sb/Sn ratio between 0.01 and 0.12, especially 0.03 to 0.07, and a thickness between 100 and 500 nm, for example between 250 and 450 nm.
Preferably the tin/antimony oxide coating layer is an exposed coating layer and the glazed panel comprises only one such tin/antimony oxide coating layer.
However, it is possible to provide one or more further coating layers, whether by pyrolysis or by other coating methods, to achieve certain desired optical qualities. It should be noted however, that the tin/antimony oxide layer when applied by pyrolysis has sufficient mechanical durability and chemical resistance to suitably serve as the exposed layer.
The panels according to the invention may be installed in single or multi-glazed assemblies. While the coated surface of the panel may be the inside surface of the exterior glazing panel so that the coated surface is not exposed to the ambient weather conditions which might otherwise more rapidly reduce its life by soiling, physical damage and/or oxidation, coatings produced by pyrolysis generally have a greater mechanical resistance than coatings produced by other methods and they may therefore be exposed to the atmosphere. The panels according to the invention may usefully be employed in laminated glass structures, for example where the coated surface is the inside surface of the exterior laminate.
According to a second aspect of the invention, there is provided a process of forming a glazing panel comprising the chemical vapour deposition of a tin/antimony oxide layer from a reactant mixture on to a vitreous substrate, said reactant mixture comprising a source of tin and a source of antimony, the Sb/Sn molar ratio in said mixture being from 0.01 to 0.5, whereby the so-coated substrate has a solar factor FS of less than 70%.
When it is desired to manufacture pyrolytically coated flat glass, it is best to do so when the glass is newly formed. To do so has economic benefits in that there is no need to reheat the glass for the pyrolytic reactions to take place, and it also has benefits as to the quality of the coating, since it is assured that the surface of the glass is in pristine condition. Preferably, therefore, said coating precursor material is brought into contact with an upper face of a hot glass substrate constituted by freshly-formed flat glass.
The invention accordingly presents the advantage of simultaneously providing a solar factor (FS) below 60%, an emissivity of less than 0.4 (preferably less than 0.3) and a luminous transmittance (TL) of more than 60%. Thus the coated product fulfil two important functions. In winter it maintains the heat in the building, because of its low emissivity. In summer it resists the passage of solar heat into the building and thus avoids overheating inside the building, thanks to its low solar factor.
This is especially achieved for coatings having an Sb/Sn ratio between 0.01 and 0.12, especially 0.03 to 0.07, and a thickness between 100 and 500 nm, for example between 250 and 450 nm.
Preferably the tin/antimony oxide coating layer is an exposed coating layer and the glazed panel comprises only one such tin/antimony oxide coating layer.
However, it is possible to provide one or more further coating layers, whether by pyrolysis or by other coating methods, to achieve certain desired optical qualities. It should be noted however, that the tin/antimony oxide layer when applied by pyrolysis has sufficient mechanical durability and chemical resistance to suitably serve as the exposed layer.
The panels according to the invention may be installed in single or multi-glazed assemblies. While the coated surface of the panel may be the inside surface of the exterior glazing panel so that the coated surface is not exposed to the ambient weather conditions which might otherwise more rapidly reduce its life by soiling, physical damage and/or oxidation, coatings produced by pyrolysis generally have a greater mechanical resistance than coatings produced by other methods and they may therefore be exposed to the atmosphere. The panels according to the invention may usefully be employed in laminated glass structures, for example where the coated surface is the inside surface of the exterior laminate.
According to a second aspect of the invention, there is provided a process of forming a glazing panel comprising the chemical vapour deposition of a tin/antimony oxide layer from a reactant mixture on to a vitreous substrate, said reactant mixture comprising a source of tin and a source of antimony, the Sb/Sn molar ratio in said mixture being from 0.01 to 0.5, whereby the so-coated substrate has a solar factor FS of less than 70%.
When it is desired to manufacture pyrolytically coated flat glass, it is best to do so when the glass is newly formed. To do so has economic benefits in that there is no need to reheat the glass for the pyrolytic reactions to take place, and it also has benefits as to the quality of the coating, since it is assured that the surface of the glass is in pristine condition. Preferably, therefore, said coating precursor material is brought into contact with an upper face of a hot glass substrate constituted by freshly-formed flat glass.
7.
Thus, the glazing panels according to the invention may be manufactured as follows. Each pyrolytic coating step may be carried out at a temperature of at least 400 C, ideally from 550 C to 750 C. The coatings can be formed on a sheet of glass which moves in a tunnel oven or on a glass ribbon during formation, whilst it is still hot. The coatings can be formed inside the lehr which follows the glass ribbon forming device or inside the float tank on the top face of the glass ribbon whilst the latter is floating on a bath of molten tin.
The coating layers are applied to the substrate by chemical vapour deposition (CVD). This is a particularly beneficial method because it provides for coatings of regular thickness and composition, such uniformity of the coating being particularly important where the product is to cover a large area. CVD offers many advantages over pyrolysis methods using sprayed liquids as the reactant materials.
With such spray methods it is difficult both- to- control the- vaporisation process and to obtain a good uniformity of coating thickness. Moreover, the pyrolysis of sprayed liquids is essentially limited to the manufacture of oxide coatings, such as SnO2 and TiO2. It is also difficult to make multi-layer coatings using sprayed liquids because every coating deposition produces a significant cooling of the substrate.
Furthermore, chemical vapour deposition is more economic in terms of raw materials, leading to lower wastage.
The product with a CVD coating is physically different from those with coatings obtained by spraying. Notably a spray coating retains traces of the sprayed droplets and of the path of the spray gun, which is not the case with CVD.
To form each coating, the substrate is brought into contact, in a coating chamber, with a gaseous medium comprising the reactant mixture in the gaseous phase. The coating chamber is fed with the reactant gas through one or more nozzles, the length of which is at least equal to the width to be coated.
Methods and devices for forming such a coating are described for example in French patent No 2 348 166 (BFG Glassgroup) or in French patent application No 2 648 453 Al (Glaverbel). These methods and devices lead to the formation of particularly strong coatings with advantageous optical properties.
To form the coatings of tin/antimony oxide, two successive nozzles are used. The reactant mixture comprising the sources of tin and antimony are fed in at the first nozzle. Where this mixture comprises chlorides which are liquid at ambient temperature, it is vaporised in a current of anhydrous carrier gas at an elevated temperature. Vaporisation is facilitated by the atomization of these reagents in the carrier gas. To produce the oxides, the chlorides are brought into the presence of water vapour conducted to the second nozzle. The water vapour is superheated and is also injected into a carrier gas.
21780,33 8.
Advantageously, nitrogen is used as the substantially inert carrier gas.
Nitrogen is sufficiently inert for the purposes in view, and it is inexpensive when compared with the noble gases.
Undercoatings of silicon oxide Si02 or SiOX may be deposited from silane SiH4 and oxygen in accordance with the descriptions in British patent specifications GB 2234264 and GB 2247691.
If a glass substrate bearing an incompletely oxidised coating is exposed to an oxidizing atmosphere for a sufficiently long period of time, it may be expected that the coating will tend to become fully oxidized so that its desired properties are lost. Therefore, such undercoat is over-coated with the tin/antimony oxide coating layer while it is still in an incompletely oxidized state, and while the substrate is still hot, thereby to preserve such undercoat in an incompletely oxidized state. The time during which the freshly undercoated glass substrate may be exposed to an oxidizing atmosphere such as air and before the undercoat is over-coated, without damaging the properties of the undercoat, will depend on the temperature of the glass during such exposure and on the nature of the undercoat.
Advantageously, said undercoating chamber is surrounded by a reducing atmosphere. The adoption of this feature assists in preventing ambient oxygen from entering the undercoating chamber and accordingly allows better control of the oxidizing conditions within that undercoating chamber.
The oxygen required for the undercoating reactions may be supplied as pure oxygen, but this adds unnecessarily to costs, and it is accordingly preferred that air is supplied to the undercoating chamber in order to introduce oxygen thereto.
It will be noted that the Sb/Sn molar ratio which is desirable in the reactant mixture does not always correspond to that ratio which is desirable for the tin/antimony coating layer Preferably the source of tin is selected from SnC4, monobutyl trichloro tin ("MBTC") and mixtures thereof. The source of antimony may be selected from SbCl5, SbCl3, organo antimony compounds and mixtures thereof. Examples of suitable source materials are Sb(OCH2CH3)36 C11.7Sb(OCH2CH3)1.3, C12SbOCHCICH3, CI2SbOCH2CHCH3CI and Cl2SbOCH2C(CH3)2C1.
The invention will now be described in more detail, with reference to the following non-limiting examples.
In the Examples the Sb/Sn molar ratio in the coating layers was determined by an X-ray analysis technique in which the number of X-ray counts of the respective elements was compared. While this technique is not as precise as if a calibration by chemical dosage were made, the similarity of antimony and tin means that they respond similarly to X-rays. The ratio of the measured number of observed 9.
counts of the respective elements thus provides a close approximation to their molar ratio.
Coloured rather than clear glass was employed as indicated in some of the Examples. The properties of the respective types of coloured glass are shown in Table 1 below. In all cases the properties were measured on glass samples having a thickness of 4 mm, this being the thickness of glass employed in all the examples except Examples 1 to 7 (for which the thicknesses are shown in Table 2). The initials in the headings to this and the other following tables (TL, TE etc.) have the meanings described above.
With regard to the calculation of the solar factor, it should be noted that for luminous transmittances (TL) below 60% the effect of low emissivity is not negligeable and should be taken into account: as the emissivity reduces so equally does the solar factor.
Table 1 Glass Type Green A Green B Grey Medium Dark Grey Grey %D in transmission (nm) 505.4/508.5 504.9/508.4 470.1/493.9 493.2/502.7 478.9/502.7 [Illuminant: C/A]
Puri (%) 2.9/3.4 2.1/2.5 1.5/0.8 5.6/5.1 2.6/1.8 TL (%) 72.66/71.12 78.44/77.20 55.65/55.56 36.80/35.76 22.41/22.30 [Illuminant: C/A
TE (%) (CIE) 44.0 52.3 56.9 25.9 31.11 FS (%) coated side 56.8 62.9 66.3 43.4 47.3 CIE) TL/FS 1.28 1.25 0.84 0.85 0.47 [Illuminant: C]
Example 1 Clear soda-lime float glass advancing at a speed of 7 metres per minute along a float chamber was undercoated at a coating station located at a position along the float chamber where the glass was at a temperature of about 700 C.
The supply line was fed with nitrogen, silane was introduced thereto with a partial pressure of 0.25%, and oxygen was introduced with a partial pressure of 0.5%
(ratio 0.5). A coating of silicon oxide Si02 having a thickness of 100 nm was obtained.
The undercoated substrate, having a thickness of 6 mm was then immediately coated by CVD pyrolysis using a coating apparatus comprising two successive nozzles. A reagent comprising a mixture of SnC4 as a source of tin and SbCl5 as a source of antimony was used. The Sb/Sn molar ratio in the mixture was 10.
about 0.2. The reactant mixture was vaporised in a current of anhydrous nitrogen gas at about 600 C, was fed in at the first nozzle. Vaporisation was facilitated by the atomization of these reagents in the carrier gas. Superheated water vapour was conducted to the second nozzle. The water vapour was heated to about 600 C, and was also injected into a carrier gas, which was air heated to about 600 C. The flow rate of gas (carrier gas + reagent) in each nozzle was 1 m3/cm width of substrate per hour, at the operating temperature.
The coating process was continued until the geometrical thickness of the tin/antimony oxide coating superimposed on the undercoated substrate was nm.
Examples 2 to 7 In Examples 2 to 7, the procedure of Example 1 was followed but with variations in such parameters as the reactant mixture, the presence or absence of an undercoat oxide, the ratio of Sb/Sn in the coating and in the reactant mixture and the thickness of the glass substrate. For instance, compared with Example 1, in Example 2 no undercoating was applied and the tin/antimony oxide coating layer had a thickness of 210 nm. The reactant mixtures were as follows:
Examples 2 and 3: the same as in Example 1 (but with a lower concentration of the reactant mixture in the carrier gas in Example 3);
Example 4: MBTC and Cl1.7Sb(OCH2CH3)1,3;
Example 5: MBTC and C12SbOCH2CHCH3Cl;
Example 6: MBTC and C12SbOCH2C(CH3)2C1;
Example 7: MBTC and SbCI3.
The variations in operating parameters for Examples 1 to 7 and the results obtained are given in the accompanying Table 2.
The glazing panels according to Examples 3 to 7 had a pleasant blue colour in transmission: the dominant wavelength in transmission in the visible wavelength lay within the range of 470 to 490 nm.
Example 6 provided a glazing panel with the combination of a low solar factor FS and low emissivity.
In a variant of Example 6 the SiO2 undercoating was replaced by an anti-reflection undercoating of silicon oxide SiOX according to the procedure of GB
patent 2247691. In another variant the Si02 undercoating was replaced by an oxidised aluminium/vanadium layer according to GB patent 2248243. In these variants the glazing panel had no purple aspect in the reflection from the uncoated side.
Example 8 Coloured float glass "Green A" advancing at a speed of 7 metres per 11.
minute along a float chamber was undercoated at a coating station located at a position along the float chamber where the glass was at a temperature of about 700 C. The supply line was fed with nitrogen, silane was introduced thereto with a partial pressure of 0.2%, and oxygen was introduced with a partial pressure of 0.5%
(ratio 0.55). A coating of silicon oxide SiOx, with x approximately equal to 1.8, was obtained with a refractive index of about 1.7. The thickness of the coating was 40 nm.
The undercoated substrate, having a thickness of 4 mm, was then coated by CVD pyrolysis. A reagent comprising a mixture of MBTC as a source of tin and Cl1.7Sb(OCH2CH3)1,3 as a source of antimony was used. The Sb/Sn molar ratio in the mixture was about 0.195 (mass ratio 0.2). The reactant mixture was vaporised in a current of anhydrous air at about 200 C, fed in at the nozzle.
Vaporisation was facilitated by the atomization of these reagents in the carrier gas.
Superheated water vapour was then introduced, heated to about 200 C.
The coating process was continued until the geometrical thickness of the tin/antimony oxide coating superimposed on the undercoated substrate was nm.
Examples 9 to 14 In Examples 9 to 14, the procedure of Example 8 was followed but with variations as shown in the accompanying Table 2 in such parameters as the thickness of the undercoat, the ratio of Sb/Sn in the coating and in the reaction mixture, the thickness of the tin/antimony oxide coating layer and the colour of the glass.
The results of examples 8 to 14 are set out in Table 3.
s The glazing panels according to the Examples 9 to 14 had a pleasant blue colour in transmission, the dominant wavelength in transmission in the visible wavelength lying within the range of 470 to 490 nm (Illuminant C).
In a variant of Example 9 in which the Green A glass was replaced by Medium Grey glass, the resultant luminous transmittance (TL) was 20%, the luminous reflectance (RL) was 10% and the energy transmission (TE) was 15 %.
Examples 15 to 30 The procedure of Example 1 was followed for further Examples 15 to 30 with variations in the reactant mixture, the colour and thickness of the glass substrate, the thickness of undercoat oxide, and the ratio of Sb/Sn in the reactant mixture and in the coating. For Examples 15 to 22 the reactant mixture was MBTC
and Cl1.7Sb(OCH2CH3)1.3 without trifluoroacetic acid whereas for Examples 23 to 30 the reactant mixture was MBTC and C11.7.Sb(OCH2CH3)1.3 with trifluoroacetic acid.
The F/Sn ratio in the reactant mixture for these examples was 0.04.
2 l 73033 12.
The variations in operating parameters, and the results obtained, are set out in the accompanying Table 4 for Examples 15 to 22 and in the accompanying Table 5 for Examples 23 to 30. The silicon oxide SiOx used in Examples 15 to 30 had a value of x approximately equal to 1.8.
Thus, the glazing panels according to the invention may be manufactured as follows. Each pyrolytic coating step may be carried out at a temperature of at least 400 C, ideally from 550 C to 750 C. The coatings can be formed on a sheet of glass which moves in a tunnel oven or on a glass ribbon during formation, whilst it is still hot. The coatings can be formed inside the lehr which follows the glass ribbon forming device or inside the float tank on the top face of the glass ribbon whilst the latter is floating on a bath of molten tin.
The coating layers are applied to the substrate by chemical vapour deposition (CVD). This is a particularly beneficial method because it provides for coatings of regular thickness and composition, such uniformity of the coating being particularly important where the product is to cover a large area. CVD offers many advantages over pyrolysis methods using sprayed liquids as the reactant materials.
With such spray methods it is difficult both- to- control the- vaporisation process and to obtain a good uniformity of coating thickness. Moreover, the pyrolysis of sprayed liquids is essentially limited to the manufacture of oxide coatings, such as SnO2 and TiO2. It is also difficult to make multi-layer coatings using sprayed liquids because every coating deposition produces a significant cooling of the substrate.
Furthermore, chemical vapour deposition is more economic in terms of raw materials, leading to lower wastage.
The product with a CVD coating is physically different from those with coatings obtained by spraying. Notably a spray coating retains traces of the sprayed droplets and of the path of the spray gun, which is not the case with CVD.
To form each coating, the substrate is brought into contact, in a coating chamber, with a gaseous medium comprising the reactant mixture in the gaseous phase. The coating chamber is fed with the reactant gas through one or more nozzles, the length of which is at least equal to the width to be coated.
Methods and devices for forming such a coating are described for example in French patent No 2 348 166 (BFG Glassgroup) or in French patent application No 2 648 453 Al (Glaverbel). These methods and devices lead to the formation of particularly strong coatings with advantageous optical properties.
To form the coatings of tin/antimony oxide, two successive nozzles are used. The reactant mixture comprising the sources of tin and antimony are fed in at the first nozzle. Where this mixture comprises chlorides which are liquid at ambient temperature, it is vaporised in a current of anhydrous carrier gas at an elevated temperature. Vaporisation is facilitated by the atomization of these reagents in the carrier gas. To produce the oxides, the chlorides are brought into the presence of water vapour conducted to the second nozzle. The water vapour is superheated and is also injected into a carrier gas.
21780,33 8.
Advantageously, nitrogen is used as the substantially inert carrier gas.
Nitrogen is sufficiently inert for the purposes in view, and it is inexpensive when compared with the noble gases.
Undercoatings of silicon oxide Si02 or SiOX may be deposited from silane SiH4 and oxygen in accordance with the descriptions in British patent specifications GB 2234264 and GB 2247691.
If a glass substrate bearing an incompletely oxidised coating is exposed to an oxidizing atmosphere for a sufficiently long period of time, it may be expected that the coating will tend to become fully oxidized so that its desired properties are lost. Therefore, such undercoat is over-coated with the tin/antimony oxide coating layer while it is still in an incompletely oxidized state, and while the substrate is still hot, thereby to preserve such undercoat in an incompletely oxidized state. The time during which the freshly undercoated glass substrate may be exposed to an oxidizing atmosphere such as air and before the undercoat is over-coated, without damaging the properties of the undercoat, will depend on the temperature of the glass during such exposure and on the nature of the undercoat.
Advantageously, said undercoating chamber is surrounded by a reducing atmosphere. The adoption of this feature assists in preventing ambient oxygen from entering the undercoating chamber and accordingly allows better control of the oxidizing conditions within that undercoating chamber.
The oxygen required for the undercoating reactions may be supplied as pure oxygen, but this adds unnecessarily to costs, and it is accordingly preferred that air is supplied to the undercoating chamber in order to introduce oxygen thereto.
It will be noted that the Sb/Sn molar ratio which is desirable in the reactant mixture does not always correspond to that ratio which is desirable for the tin/antimony coating layer Preferably the source of tin is selected from SnC4, monobutyl trichloro tin ("MBTC") and mixtures thereof. The source of antimony may be selected from SbCl5, SbCl3, organo antimony compounds and mixtures thereof. Examples of suitable source materials are Sb(OCH2CH3)36 C11.7Sb(OCH2CH3)1.3, C12SbOCHCICH3, CI2SbOCH2CHCH3CI and Cl2SbOCH2C(CH3)2C1.
The invention will now be described in more detail, with reference to the following non-limiting examples.
In the Examples the Sb/Sn molar ratio in the coating layers was determined by an X-ray analysis technique in which the number of X-ray counts of the respective elements was compared. While this technique is not as precise as if a calibration by chemical dosage were made, the similarity of antimony and tin means that they respond similarly to X-rays. The ratio of the measured number of observed 9.
counts of the respective elements thus provides a close approximation to their molar ratio.
Coloured rather than clear glass was employed as indicated in some of the Examples. The properties of the respective types of coloured glass are shown in Table 1 below. In all cases the properties were measured on glass samples having a thickness of 4 mm, this being the thickness of glass employed in all the examples except Examples 1 to 7 (for which the thicknesses are shown in Table 2). The initials in the headings to this and the other following tables (TL, TE etc.) have the meanings described above.
With regard to the calculation of the solar factor, it should be noted that for luminous transmittances (TL) below 60% the effect of low emissivity is not negligeable and should be taken into account: as the emissivity reduces so equally does the solar factor.
Table 1 Glass Type Green A Green B Grey Medium Dark Grey Grey %D in transmission (nm) 505.4/508.5 504.9/508.4 470.1/493.9 493.2/502.7 478.9/502.7 [Illuminant: C/A]
Puri (%) 2.9/3.4 2.1/2.5 1.5/0.8 5.6/5.1 2.6/1.8 TL (%) 72.66/71.12 78.44/77.20 55.65/55.56 36.80/35.76 22.41/22.30 [Illuminant: C/A
TE (%) (CIE) 44.0 52.3 56.9 25.9 31.11 FS (%) coated side 56.8 62.9 66.3 43.4 47.3 CIE) TL/FS 1.28 1.25 0.84 0.85 0.47 [Illuminant: C]
Example 1 Clear soda-lime float glass advancing at a speed of 7 metres per minute along a float chamber was undercoated at a coating station located at a position along the float chamber where the glass was at a temperature of about 700 C.
The supply line was fed with nitrogen, silane was introduced thereto with a partial pressure of 0.25%, and oxygen was introduced with a partial pressure of 0.5%
(ratio 0.5). A coating of silicon oxide Si02 having a thickness of 100 nm was obtained.
The undercoated substrate, having a thickness of 6 mm was then immediately coated by CVD pyrolysis using a coating apparatus comprising two successive nozzles. A reagent comprising a mixture of SnC4 as a source of tin and SbCl5 as a source of antimony was used. The Sb/Sn molar ratio in the mixture was 10.
about 0.2. The reactant mixture was vaporised in a current of anhydrous nitrogen gas at about 600 C, was fed in at the first nozzle. Vaporisation was facilitated by the atomization of these reagents in the carrier gas. Superheated water vapour was conducted to the second nozzle. The water vapour was heated to about 600 C, and was also injected into a carrier gas, which was air heated to about 600 C. The flow rate of gas (carrier gas + reagent) in each nozzle was 1 m3/cm width of substrate per hour, at the operating temperature.
The coating process was continued until the geometrical thickness of the tin/antimony oxide coating superimposed on the undercoated substrate was nm.
Examples 2 to 7 In Examples 2 to 7, the procedure of Example 1 was followed but with variations in such parameters as the reactant mixture, the presence or absence of an undercoat oxide, the ratio of Sb/Sn in the coating and in the reactant mixture and the thickness of the glass substrate. For instance, compared with Example 1, in Example 2 no undercoating was applied and the tin/antimony oxide coating layer had a thickness of 210 nm. The reactant mixtures were as follows:
Examples 2 and 3: the same as in Example 1 (but with a lower concentration of the reactant mixture in the carrier gas in Example 3);
Example 4: MBTC and Cl1.7Sb(OCH2CH3)1,3;
Example 5: MBTC and C12SbOCH2CHCH3Cl;
Example 6: MBTC and C12SbOCH2C(CH3)2C1;
Example 7: MBTC and SbCI3.
The variations in operating parameters for Examples 1 to 7 and the results obtained are given in the accompanying Table 2.
The glazing panels according to Examples 3 to 7 had a pleasant blue colour in transmission: the dominant wavelength in transmission in the visible wavelength lay within the range of 470 to 490 nm.
Example 6 provided a glazing panel with the combination of a low solar factor FS and low emissivity.
In a variant of Example 6 the SiO2 undercoating was replaced by an anti-reflection undercoating of silicon oxide SiOX according to the procedure of GB
patent 2247691. In another variant the Si02 undercoating was replaced by an oxidised aluminium/vanadium layer according to GB patent 2248243. In these variants the glazing panel had no purple aspect in the reflection from the uncoated side.
Example 8 Coloured float glass "Green A" advancing at a speed of 7 metres per 11.
minute along a float chamber was undercoated at a coating station located at a position along the float chamber where the glass was at a temperature of about 700 C. The supply line was fed with nitrogen, silane was introduced thereto with a partial pressure of 0.2%, and oxygen was introduced with a partial pressure of 0.5%
(ratio 0.55). A coating of silicon oxide SiOx, with x approximately equal to 1.8, was obtained with a refractive index of about 1.7. The thickness of the coating was 40 nm.
The undercoated substrate, having a thickness of 4 mm, was then coated by CVD pyrolysis. A reagent comprising a mixture of MBTC as a source of tin and Cl1.7Sb(OCH2CH3)1,3 as a source of antimony was used. The Sb/Sn molar ratio in the mixture was about 0.195 (mass ratio 0.2). The reactant mixture was vaporised in a current of anhydrous air at about 200 C, fed in at the nozzle.
Vaporisation was facilitated by the atomization of these reagents in the carrier gas.
Superheated water vapour was then introduced, heated to about 200 C.
The coating process was continued until the geometrical thickness of the tin/antimony oxide coating superimposed on the undercoated substrate was nm.
Examples 9 to 14 In Examples 9 to 14, the procedure of Example 8 was followed but with variations as shown in the accompanying Table 2 in such parameters as the thickness of the undercoat, the ratio of Sb/Sn in the coating and in the reaction mixture, the thickness of the tin/antimony oxide coating layer and the colour of the glass.
The results of examples 8 to 14 are set out in Table 3.
s The glazing panels according to the Examples 9 to 14 had a pleasant blue colour in transmission, the dominant wavelength in transmission in the visible wavelength lying within the range of 470 to 490 nm (Illuminant C).
In a variant of Example 9 in which the Green A glass was replaced by Medium Grey glass, the resultant luminous transmittance (TL) was 20%, the luminous reflectance (RL) was 10% and the energy transmission (TE) was 15 %.
Examples 15 to 30 The procedure of Example 1 was followed for further Examples 15 to 30 with variations in the reactant mixture, the colour and thickness of the glass substrate, the thickness of undercoat oxide, and the ratio of Sb/Sn in the reactant mixture and in the coating. For Examples 15 to 22 the reactant mixture was MBTC
and Cl1.7Sb(OCH2CH3)1.3 without trifluoroacetic acid whereas for Examples 23 to 30 the reactant mixture was MBTC and C11.7.Sb(OCH2CH3)1.3 with trifluoroacetic acid.
The F/Sn ratio in the reactant mixture for these examples was 0.04.
2 l 73033 12.
The variations in operating parameters, and the results obtained, are set out in the accompanying Table 4 for Examples 15 to 22 and in the accompanying Table 5 for Examples 23 to 30. The silicon oxide SiOx used in Examples 15 to 30 had a value of x approximately equal to 1.8.
13.
Table 2 Example 1 2 3 4 5 6 7 Tin/antimony oxide thickness (nm) 185 210 105 120 105 445 110 Undercoat oxide Si02 absent absent SiO2 Si02 SiO2 Si02 Undercoat thickness (nm) 100 0 0 70 70 70 70 Sb/Sn ratio in coating 0.48 0.48 0.46 0.19 0.15 0.06 0.18 Sb/Sn ratio in reactants 0.20 0.20 0.20 0.20 0.20 0.10 0.20 Haze (%) 0.07 2.09 4.36 to 7.01 low low low low N
TL (%) 45.7 44.3 65.5 51.0 61.6 47.5 55.0 --i RL (%) (coated side) 9.0 12.0 18.8 12.0 11.7 6.6 13.7 co t.N
FS (%) (coated side) (CIE) 55.3 56.9 66.0 58.4 62.2 47.2 59.6 TUFS 0.83 0.78 0.99 0.87 0.99 1.01 0.92 ~.p in transmission (nm) 587.5 -560 480.1 478.8 481.0 483.0 479.3 Colour purity in transmission (%) 3.4 3.9 4.9 11.5 8.7 8.0 10.3 %.p in reflection from the coated side (nm) 472.3 494.5 575.3 579.5 577.6 490.0 577.0 Colour purity (%) in reflection froin the 36.9 7.0 19.1 35.0 35.2 6.0 33.1 coated side Emissivity >0.7 >0.7 >0.7 0.84 0.71 0.25 0.79 Glass thickness (m-n) 6 6 6 5 5 5 5 14.
Table 3 Example 8 9 10 11 I2 13 14 Tin/antimony oxide thickness (nm) 120 120 320 470 470 320 470 Undercoat oxide Si02 Si02 SiO2 SiO2 SiO2 SiO2 SiO2 Undercoat thickness (nm) 40 70 40 40 40 40 40 Sb/Sn ratio in coating 0.10 0.18 0.09 0.09 0.09 0.09 0.09 Sb/Sn ratio in reactants 0.07 0.20 0.07 0.07 0.07 0.07 0.07 Haze (%) 0.36 0.1 1.0 1.8 1.8 1.0 1.8 TL (%) [Illuminant A/Illuminant C] 53/55 39/20 31/32 31/32 9/9 40/41 36 [A] N
RL (%) (coated side) [Illuminant A/C] 9/10 11/11 7/7 7/7 7/7 8/7 7 [A] Co RL (%) (uncoated side) [Illuminant C] 8 8 6 6 5 7 - C=) TE (%) (CIE) 31 25 25 18 9 21 27 FS (%) (coated side) (CIE) 45 41 41 36 29 39 43 TUFS 1.2/1.2 0.95/0.98 0.76/0.78 0.86/0.89 0.31/0.31 1.02/1.05 5.4 [A]
2.p in transmission (nm) 505.5/498.6 497.2/487.0 494.8/481.9 497.2/487.2 494.2/480.0 501.0/491.6 493.4 [A]
Colour purity in transmission (%) 4.4/4.2 6.2/8.9 4.9/8.1 7.6/10.8 7.0/11.8 7.2/8.6 5.4 [A]
~.p in reflection from the coated side (nm) 487.9/478.1 -572.5/566.9 -511.8/512.2 -576.9/559.8 -555.4/550.1 -512.5/513.6 -576.0 [A]
Colour purity (%) in reflection from the 7.4/14.6 2.2/2.9 17.2/16.3 6.0/1.2 2.1/6.6 15.4/14.5 1.5 [A]
coated side Emissivity 0.71 0.85 0.44 0.35 0.35 0.44 0.35 Colour of glass Green A Green A Grey Green B Dark grey Green A Clear soda lime 15. ' Table 4 Example 15 16 17 18 19 20 21 22 Tin/antimony oxide thickness (nm) 320 320 320 320 390 390 390 390 Undercoat oxide SiOx SiO., SiO, SiOX SiOX SiOX SiOX SiOx Undercoat thickness (nm) 60 (approx) 60 (approx) 60 (approx) 60 (approx) 80 (approx) 80 (approx) 80 (approx) 80 (approx) Sb/Sn ratio in coating 0.053 0.053 0.053 0.053 0.058 0.058 0.058 0.058 Sb/Sn ratio in reactants 0.028 0.028 0.028 0.028 0.028 0.028 0.028 0.028 Haze (%) 0.65 0.65 0.65 0.65 1.2 1.2 1.2 1.2 TL (%) filluminant C] 68.8 55.7 60.1 28.2 61.0 49.2 25.0 53.1 N
RL (%) (coated side) 8.9 8.2 8.4 7.2 9.0 8.0 7.2 6.9 RL (%) (uncoated side) 8.9 7.3 7.8 5.0 7.8 6.5 4.8 8.2 Gt7 CD
TE (%) (CIE) 50.8 28.3 33.1 15.8 43.0 24.5 13.7 28.5 cs., FS (%) (coated side) (CIE) 60.3 43.6 47.2 34.4 54.7 40.9 32.9 40.1 TL/TE 1.35 2.00 1.82 1.75 1.42 1.96 1.79 1.86 TUFS 1.15 1.27 1.28 0.82 1.11 1.20 0.76 1.20 ?1p in transmission (nm) 524.0 506.2 506.0 494.0 496.0 500.7 493.4 499.5 Colour purity in transmission (%) 0.5 3.1 2.3 5.8 2.2 4.7 7.5 4.1 ?.p in reflection from the coated side (nm) 482.9 484.2 484.0 482.9 -495.2 -493.8 -495.0 -550.3 Colour purity (%) in reflectioti from the 14.5 16.2 15.8 18.0 5.0 4.4 6.4 7.0 coated side Einissivity 0.29 0.29 0.29 0.29 0.27 0.27 0.27 0.27 Colour of glass Clear Green A Green B Med. grey Clear Green A Med. grey Green B
Table 2 Example 1 2 3 4 5 6 7 Tin/antimony oxide thickness (nm) 185 210 105 120 105 445 110 Undercoat oxide Si02 absent absent SiO2 Si02 SiO2 Si02 Undercoat thickness (nm) 100 0 0 70 70 70 70 Sb/Sn ratio in coating 0.48 0.48 0.46 0.19 0.15 0.06 0.18 Sb/Sn ratio in reactants 0.20 0.20 0.20 0.20 0.20 0.10 0.20 Haze (%) 0.07 2.09 4.36 to 7.01 low low low low N
TL (%) 45.7 44.3 65.5 51.0 61.6 47.5 55.0 --i RL (%) (coated side) 9.0 12.0 18.8 12.0 11.7 6.6 13.7 co t.N
FS (%) (coated side) (CIE) 55.3 56.9 66.0 58.4 62.2 47.2 59.6 TUFS 0.83 0.78 0.99 0.87 0.99 1.01 0.92 ~.p in transmission (nm) 587.5 -560 480.1 478.8 481.0 483.0 479.3 Colour purity in transmission (%) 3.4 3.9 4.9 11.5 8.7 8.0 10.3 %.p in reflection from the coated side (nm) 472.3 494.5 575.3 579.5 577.6 490.0 577.0 Colour purity (%) in reflection froin the 36.9 7.0 19.1 35.0 35.2 6.0 33.1 coated side Emissivity >0.7 >0.7 >0.7 0.84 0.71 0.25 0.79 Glass thickness (m-n) 6 6 6 5 5 5 5 14.
Table 3 Example 8 9 10 11 I2 13 14 Tin/antimony oxide thickness (nm) 120 120 320 470 470 320 470 Undercoat oxide Si02 Si02 SiO2 SiO2 SiO2 SiO2 SiO2 Undercoat thickness (nm) 40 70 40 40 40 40 40 Sb/Sn ratio in coating 0.10 0.18 0.09 0.09 0.09 0.09 0.09 Sb/Sn ratio in reactants 0.07 0.20 0.07 0.07 0.07 0.07 0.07 Haze (%) 0.36 0.1 1.0 1.8 1.8 1.0 1.8 TL (%) [Illuminant A/Illuminant C] 53/55 39/20 31/32 31/32 9/9 40/41 36 [A] N
RL (%) (coated side) [Illuminant A/C] 9/10 11/11 7/7 7/7 7/7 8/7 7 [A] Co RL (%) (uncoated side) [Illuminant C] 8 8 6 6 5 7 - C=) TE (%) (CIE) 31 25 25 18 9 21 27 FS (%) (coated side) (CIE) 45 41 41 36 29 39 43 TUFS 1.2/1.2 0.95/0.98 0.76/0.78 0.86/0.89 0.31/0.31 1.02/1.05 5.4 [A]
2.p in transmission (nm) 505.5/498.6 497.2/487.0 494.8/481.9 497.2/487.2 494.2/480.0 501.0/491.6 493.4 [A]
Colour purity in transmission (%) 4.4/4.2 6.2/8.9 4.9/8.1 7.6/10.8 7.0/11.8 7.2/8.6 5.4 [A]
~.p in reflection from the coated side (nm) 487.9/478.1 -572.5/566.9 -511.8/512.2 -576.9/559.8 -555.4/550.1 -512.5/513.6 -576.0 [A]
Colour purity (%) in reflection from the 7.4/14.6 2.2/2.9 17.2/16.3 6.0/1.2 2.1/6.6 15.4/14.5 1.5 [A]
coated side Emissivity 0.71 0.85 0.44 0.35 0.35 0.44 0.35 Colour of glass Green A Green A Grey Green B Dark grey Green A Clear soda lime 15. ' Table 4 Example 15 16 17 18 19 20 21 22 Tin/antimony oxide thickness (nm) 320 320 320 320 390 390 390 390 Undercoat oxide SiOx SiO., SiO, SiOX SiOX SiOX SiOX SiOx Undercoat thickness (nm) 60 (approx) 60 (approx) 60 (approx) 60 (approx) 80 (approx) 80 (approx) 80 (approx) 80 (approx) Sb/Sn ratio in coating 0.053 0.053 0.053 0.053 0.058 0.058 0.058 0.058 Sb/Sn ratio in reactants 0.028 0.028 0.028 0.028 0.028 0.028 0.028 0.028 Haze (%) 0.65 0.65 0.65 0.65 1.2 1.2 1.2 1.2 TL (%) filluminant C] 68.8 55.7 60.1 28.2 61.0 49.2 25.0 53.1 N
RL (%) (coated side) 8.9 8.2 8.4 7.2 9.0 8.0 7.2 6.9 RL (%) (uncoated side) 8.9 7.3 7.8 5.0 7.8 6.5 4.8 8.2 Gt7 CD
TE (%) (CIE) 50.8 28.3 33.1 15.8 43.0 24.5 13.7 28.5 cs., FS (%) (coated side) (CIE) 60.3 43.6 47.2 34.4 54.7 40.9 32.9 40.1 TL/TE 1.35 2.00 1.82 1.75 1.42 1.96 1.79 1.86 TUFS 1.15 1.27 1.28 0.82 1.11 1.20 0.76 1.20 ?1p in transmission (nm) 524.0 506.2 506.0 494.0 496.0 500.7 493.4 499.5 Colour purity in transmission (%) 0.5 3.1 2.3 5.8 2.2 4.7 7.5 4.1 ?.p in reflection from the coated side (nm) 482.9 484.2 484.0 482.9 -495.2 -493.8 -495.0 -550.3 Colour purity (%) in reflectioti from the 14.5 16.2 15.8 18.0 5.0 4.4 6.4 7.0 coated side Einissivity 0.29 0.29 0.29 0.29 0.27 0.27 0.27 0.27 Colour of glass Clear Green A Green B Med. grey Clear Green A Med. grey Green B
16.
Table 5 Example 23 24 25 26 27 28 29 30 Tin/antimony oxide thickness (nm) 290 290 290 290 410 410 410 410 Undercoat oxide SiOx SiOX SiOx SiOx SiOX SiOX SiOx SiOX
Undercoat thickness (nm) 80 (approx) 80 (approx) 80 (approx) 80 (approx) 90 (approx) 90 (approx) 90 (approx) 90 (approx) Sb/Sn ratio in coating 0.038 0.038 0.038 0.038 0.037 0.037 0.037 0.037 Sb/Sn ratio in reactants 0.028 0.028 0.028 0.028 0.028 0.028 0.028 0.028 Haze (%) 0.82 0.82 0.82 0.82 1.2 1.2 1.2 1.2 TL (%) [Illuminant C] 70.2 56.7 61.0 28.7 64.2 51.9 26.9 56.4 RL (%) (coated side) 10.0 9.0 9.2 8.0 8.8 8.1 7.2 8.3 RL (%) (uncoated side) 9.5 8.0 8.3 5.2 7.7 6.6 4.8 6.9 TE (%) (CIE) 54.3 29.5 34.7 16.6 47.2 26.1 14.6 30.6 FS (%) (coated side) (CIE) 63.0 44.5 48.3 34.9 57.7 42.0 33.6 45.4 TVTE 1.30 1.90 1.74 1.71 1.36 2.00 1.73 1.81 TUFS 1.11 1.27 1.27 0.83 1.10 1.24 0.76 1.24 Xp in tratrsmission (nin) 581.3 538.8 549.4 498.5 568.6 535.9 502.7 543.7 Colour purity in transmission (%) 2.9 2.9 2.7 3.3 3.5 3.7 3.6 3.5 n,p in reflection from the coated side (nm) 510.3 508.6 508.9 507.2 549.3 505.1 491.8 507.0 Colour purity (%) in reflection from the 8.1 10.1 9.6 11.3 3.3 1.1 1.2 1.0 coated side Emissivity 0.28 0.28 0.28 0.28 0.23 0.23 0.23 0.23 Colour of glass Clear Green A Green B Med. grey Clear Green A Med. grey Green B
Table 5 Example 23 24 25 26 27 28 29 30 Tin/antimony oxide thickness (nm) 290 290 290 290 410 410 410 410 Undercoat oxide SiOx SiOX SiOx SiOx SiOX SiOX SiOx SiOX
Undercoat thickness (nm) 80 (approx) 80 (approx) 80 (approx) 80 (approx) 90 (approx) 90 (approx) 90 (approx) 90 (approx) Sb/Sn ratio in coating 0.038 0.038 0.038 0.038 0.037 0.037 0.037 0.037 Sb/Sn ratio in reactants 0.028 0.028 0.028 0.028 0.028 0.028 0.028 0.028 Haze (%) 0.82 0.82 0.82 0.82 1.2 1.2 1.2 1.2 TL (%) [Illuminant C] 70.2 56.7 61.0 28.7 64.2 51.9 26.9 56.4 RL (%) (coated side) 10.0 9.0 9.2 8.0 8.8 8.1 7.2 8.3 RL (%) (uncoated side) 9.5 8.0 8.3 5.2 7.7 6.6 4.8 6.9 TE (%) (CIE) 54.3 29.5 34.7 16.6 47.2 26.1 14.6 30.6 FS (%) (coated side) (CIE) 63.0 44.5 48.3 34.9 57.7 42.0 33.6 45.4 TVTE 1.30 1.90 1.74 1.71 1.36 2.00 1.73 1.81 TUFS 1.11 1.27 1.27 0.83 1.10 1.24 0.76 1.24 Xp in tratrsmission (nin) 581.3 538.8 549.4 498.5 568.6 535.9 502.7 543.7 Colour purity in transmission (%) 2.9 2.9 2.7 3.3 3.5 3.7 3.6 3.5 n,p in reflection from the coated side (nm) 510.3 508.6 508.9 507.2 549.3 505.1 491.8 507.0 Colour purity (%) in reflection from the 8.1 10.1 9.6 11.3 3.3 1.1 1.2 1.0 coated side Emissivity 0.28 0.28 0.28 0.28 0.23 0.23 0.23 0.23 Colour of glass Clear Green A Green B Med. grey Clear Green A Med. grey Green B
Claims (38)
1. A glazing panel comprising a vitreous substrate carrying a tin/antimony oxide coating layer containing tin and antimony in a Sb/Sn molar ratio of from 0.01 to 0.5, the said coating layer having been pyrolytically formed by chemical vapour deposition, and a coating layer comprising tin oxide doped with fluorine, whereby the so-coated substrate has a solar factor (FS) of less than 70%.
2. A glazing panel according to claim 1, wherein the Sb/Sn molar ratio ranges from 0.03 to 0.21.
3. A glazing panel according to claim 2, wherein the Sb/Sn molar ratio ranges from 0.03 to 0.15.
4. A glazing panel according to any one of claims 1 to 3, wherein an intermediate haze-reducing coating layer is positioned between the substrate and the tin/antimony oxide coating layer.
5. A glazing panel according to claim 4, wherein the said haze-reducing coating layer comprises silicon oxide.
6. A glazing panel according to any one of claims 1 to 5, wherein the solar factor (FS) is less than 60%.
7. A glazing panel according to any one of claims 1 to 6, having a luminous transmittance (TL) of between 40 and 65%.
8. A glazing panel according to any one of claims 1 to 7, wherein the said tin/antimony oxide coating layer has a thickness of from 100 to 500 nm.
9. A glazing panel according to claim 8, wherein the tin/antimony oxide coating layer has a thickness of from 250 to 450 nm.
10. A glazing panel according to any one of claims 1 to 9, wherein the vitreous substrate is selected from the group comprising clear glass and coloured glass.
11. A glazing panel according to any one of claims 1 to 10, having a luminous reflectance (RL) of less than 11%.
12. A solar control glazing panel, having a solar factor (FS) of less than 70%
and an emissivity of less than 0.4, comprising a soda-lime float glass substrate carrying a coating which comprises a plurality of coating layers comprising:
- a first coating layer having been pyrolytically formed from reactants in a gaseous phase, comprising tin and antimony oxides and having a Sb/Sn molar ratio ranging from 0.03 to 0.15;
- a second coating layer, positioned on the first coating layer and comprising tin oxide doped with fluorine;
wherein the coating, excluding the second coating layer, is conferring on a 4 mm thick sheet of clear soda-lime glass a solar energy transmission (TE) measured according to the CIE standard of at least 27%.
and an emissivity of less than 0.4, comprising a soda-lime float glass substrate carrying a coating which comprises a plurality of coating layers comprising:
- a first coating layer having been pyrolytically formed from reactants in a gaseous phase, comprising tin and antimony oxides and having a Sb/Sn molar ratio ranging from 0.03 to 0.15;
- a second coating layer, positioned on the first coating layer and comprising tin oxide doped with fluorine;
wherein the coating, excluding the second coating layer, is conferring on a 4 mm thick sheet of clear soda-lime glass a solar energy transmission (TE) measured according to the CIE standard of at least 27%.
13. A glazing panel according to claim 12, wherein the coating, excluding the second coating layer, is conferring on a 4 mm thick sheet of clear soda-lime glass a solar energy transmission (TE) measured according to the CIE standard ranging from 27 to 54.3%.
14. A glazing panel according to any one of claims 12 to 13, wherein the coating, excluding the second coating layer, is conferring on a 4 mm thick sheet of clear soda-lime glass a solar factor (FS) according to the CIE standard (coated side) ranging from 43 to 63%.
15. A glazing panel according to any one of claims 12 to 14, having a luminous transmittance (TL) measured under CIE standard Illuminant C of between 40 to 65%.
16. A glazing panel according to any one of claims 12 to 15, wherein the first coating layer has a thickness of from 100 to 500 nm.
17. A glazing panel according to any one of claims 12 to 16, wherein at least one intermediate coating layer is positioned between the substrate and the first coating layer.
18. A glazing panel according to claim 17, wherein the at least one intermediate coating layer is selected from the group consisting of a haze-reducing coating layer, an anti-reflection undercoat and a silicon oxide undercoat.
19. A glazing panel according to any one of claims 17 to 18, wherein the glazing panel has a luminous transmittance (TL) measured under CIE standard Illuminant C of between 40 and 65%
and comprises at least one intermediate coating layer on the soda-lime glass substrate, the at least one intermediate coating layer being positioned on the one side of the glass substrate in between the one side of the glass substrate and the first coating layer, and the second coating layer being positioned over the first coating layer, wherein the combination of the at least one intermediate coating layer and the first coating layer comprising tin and antimony oxides is conferring on a 4 mm thick sheet of clear soda-lime glass a solar factor (FS) according to the CIE standard (coated side) ranging from 43 to 63%.
and comprises at least one intermediate coating layer on the soda-lime glass substrate, the at least one intermediate coating layer being positioned on the one side of the glass substrate in between the one side of the glass substrate and the first coating layer, and the second coating layer being positioned over the first coating layer, wherein the combination of the at least one intermediate coating layer and the first coating layer comprising tin and antimony oxides is conferring on a 4 mm thick sheet of clear soda-lime glass a solar factor (FS) according to the CIE standard (coated side) ranging from 43 to 63%.
20. A solar control glazing panel, having a solar factor (FS) of less than 70%
and an emissivity of less than 0.4, comprising a soda-lime float glass substrate carrying a coating which comprises a plurality of coating layers comprising:
- a first coating layer having been pyrolytically formed from reactants in a gaseous phase, comprising tin and antimony oxides and having a Sb/Sn molar ratio ranging from 0.03 to 0.15;
- a second coating layer, positioned on the first coating layer and comprising tin oxide doped with fluorine;
wherein the solar control glazing panel without the second coating layer has a solar energy transmission (TE) measured according to the CIE standard of at least 15.8%.
and an emissivity of less than 0.4, comprising a soda-lime float glass substrate carrying a coating which comprises a plurality of coating layers comprising:
- a first coating layer having been pyrolytically formed from reactants in a gaseous phase, comprising tin and antimony oxides and having a Sb/Sn molar ratio ranging from 0.03 to 0.15;
- a second coating layer, positioned on the first coating layer and comprising tin oxide doped with fluorine;
wherein the solar control glazing panel without the second coating layer has a solar energy transmission (TE) measured according to the CIE standard of at least 15.8%.
21. A glazing panel according to claim 20, wherein the glazing panel without the second coating layer has a solar energy transmission (TE) measured according to the CIE standard ranging from 15.8 to 54.3%.
22. A glazing panel according to claim 21, wherein the glazing panel without the second coating layer has a solar energy transmission (TE) measured according to the CIE standard ranging from 34.7 to 50.8%.
23. A glazing panel according to any one of claims 20 to 22, wherein the glazing panel without the second coating layer has a solar factor (FS) ranging from 34.4 to 63%.
24. A glazing panel according to any one of claims 20 to 23, having a luminous transmittance (TL) measured under CIE standard Illuminant C of between 40 and 65%.
25. A glazing panel according to any one of claims 20 to 24, wherein the first coating layer has a thickness of from 100 to 500 nm.
26. A glazing panel according to any one of claims 20 to 25, wherein at least one intermediate coating layer is positioned between the substrate and the first coating layer.
27. A glazing panel according to claim 26, wherein the at least one intermediate coating layer is selected from the group consisting of a haze-reducing coating layer, an anti-reflection undercoat and a silicon oxide undercoat.
28. A glazing panel according to any one of claims 20 to 27, wherein the glass substrate has a thickness of 4 mm.
29. A glazing panel according to any one of claims 20 to 28, wherein the glass substrate is selected from the group consisting of clear glass substrates and coloured glass substrates.
30. A glazing panel according to any one of claims 26 to 29, wherein the glazing panel has a luminous transmittance (TL) measured under CIE standard Illuminant C of between 40 and 65%
and comprises at least one intermediate coating layer on the soda-lime glass substrate, the at least one intermediate coating layer being positioned on the one side of the glass substrate in between the one side of the glass substrate and the first coating layer, and the second coating layer being positioned over the first coating layer, wherein the combination of the glass substrate, the at least one intermediate coating layer and the first coating layer comprising tin and antimony oxides has a solar factor (FS) according to the CIE standard (coated side) ranging from 34.4 to 63% and wherein the first coating has a thickness ranging from 100 to 500 nm.
and comprises at least one intermediate coating layer on the soda-lime glass substrate, the at least one intermediate coating layer being positioned on the one side of the glass substrate in between the one side of the glass substrate and the first coating layer, and the second coating layer being positioned over the first coating layer, wherein the combination of the glass substrate, the at least one intermediate coating layer and the first coating layer comprising tin and antimony oxides has a solar factor (FS) according to the CIE standard (coated side) ranging from 34.4 to 63% and wherein the first coating has a thickness ranging from 100 to 500 nm.
31. A solar control glazing panel for the exterior facade of a building, the glazing panel transmitting visible light in order to allow natural illumination of the interior of the building and in order to allow occupants of the building to see out and providing a combination of low solar factor and low emissivity, comprising a soda-lime float glass substrate carrying a coating which comprises a plurality of coating layers comprising:
- a first coating layer having been pyrolytically formed from reactants in a gaseous phase, comprising tin and antimony oxides and having a Sb/Sn molar ratio ranging from 0.03 to 0.15;
- a second coating layer, positioned on the first coating layer and comprising tin oxide doped with fluorine;
- at least one intermediate coating layer, on the soda-lime glass substrate, the at least one intermediate coating layer being positioned on the one side of the glass substrate in between the one side of the glass substrate and the first coating layer, and the second coating layer being positioned over the first coating layer;
the glazing panel having:
- transmission of visible light characterised by a luminous transmittance (TL) measured under CIE standard Illuminant C of from 40 to 65%;
- a combination of a low solar factor and low emissivity characterised by a solar factor (FS) of less than 70% and an emissivity of less than 0.4.
- a first coating layer having been pyrolytically formed from reactants in a gaseous phase, comprising tin and antimony oxides and having a Sb/Sn molar ratio ranging from 0.03 to 0.15;
- a second coating layer, positioned on the first coating layer and comprising tin oxide doped with fluorine;
- at least one intermediate coating layer, on the soda-lime glass substrate, the at least one intermediate coating layer being positioned on the one side of the glass substrate in between the one side of the glass substrate and the first coating layer, and the second coating layer being positioned over the first coating layer;
the glazing panel having:
- transmission of visible light characterised by a luminous transmittance (TL) measured under CIE standard Illuminant C of from 40 to 65%;
- a combination of a low solar factor and low emissivity characterised by a solar factor (FS) of less than 70% and an emissivity of less than 0.4.
32. A glazing panel according to claim 31, wherein the at least one intermediate coating layer is selected from the group consisting of a haze-reducing coating layer, an anti-reflection undercoat and a silicon oxide undercoat.
33. A glazing panel according to any of claims 31 to 32, wherein the glass substrate is selected from the group consisting of glass substrates having a thickness of 4 mm, glass substrates having a thickness of 5 mm and glass substrates having a thickness of 6 mm.
34. A glazing panel according to any of claims 31 to 33, wherein the glass substrate is selected from the group consisting of clear glass substrates and coloured glass substrates.
35. A glazing panel according to any one of claims 31 to 34, wherein the first coating layer has a thickness of from 100 to 500 nm.
36. A glazing panel according to any one of claims 31 to 35, wherein the combination of the glass substrate, the at least one intermediate coating layer and the first coating layer comprising tin and antimony oxides has a solar energy transmission (TE) according to the CIE standard of at least 15.8%.
37. A glazing panel according to claim 36, wherein the combination of the glass substrate, the at least one intermediate coating layer and the first coating layer comprising tin and antimony oxides has a solar energy transmission (TE) according to the CE standard ranging from 15.8 to 54.3%.
38. A glazing panel having:
- a solar factor (FS) according to the CIE standard (coated side) less than 60%;
- a luminous transmittance (TL) measured under CIE standard Illuminant C of from 40 to 65%;
- a luminous reflectance (RL) of less than 11 %; and -a solar energy transmission (TE) measured according to the CIE standard of at least 27%, wherein the glazing panel comprises a vitreous substrate comprising a soda-lime float glass substrate carrying a coating which comprises a plurality of coating layers comprising, in order:
- at least one intermediate coating layer;
- a first coating layer having been pyrolytically formed from reactants in a gaseous phase, comprising tin and antimony oxides and having a Sb/Sn molar ratio ranging from 0.03 to 0.15 and a thickness of from 100 to 500 nm;
- a second coating layer, positioned on the first coating layer and comprising tin oxide doped with fluorine.
- a solar factor (FS) according to the CIE standard (coated side) less than 60%;
- a luminous transmittance (TL) measured under CIE standard Illuminant C of from 40 to 65%;
- a luminous reflectance (RL) of less than 11 %; and -a solar energy transmission (TE) measured according to the CIE standard of at least 27%, wherein the glazing panel comprises a vitreous substrate comprising a soda-lime float glass substrate carrying a coating which comprises a plurality of coating layers comprising, in order:
- at least one intermediate coating layer;
- a first coating layer having been pyrolytically formed from reactants in a gaseous phase, comprising tin and antimony oxides and having a Sb/Sn molar ratio ranging from 0.03 to 0.15 and a thickness of from 100 to 500 nm;
- a second coating layer, positioned on the first coating layer and comprising tin oxide doped with fluorine.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CA002607846A CA2607846A1 (en) | 1995-06-09 | 1996-06-03 | Glazing panel having solar screening properties and a process for making such a panel |
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GB9511691.9 | 1995-06-09 | ||
| GBGB9511691.9A GB9511691D0 (en) | 1995-06-09 | 1995-06-09 | A glazing panel having solar screening properties and a process for making such a panel |
| GBGB9514190.9A GB9514190D0 (en) | 1995-07-12 | 1995-07-12 | A glazing panel having solar screening properties and a process for making such a panel |
| GB9514190.9 | 1995-07-12 |
Related Child Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002607846A Division CA2607846A1 (en) | 1995-06-09 | 1996-06-03 | Glazing panel having solar screening properties and a process for making such a panel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2178033A1 CA2178033A1 (en) | 1996-12-10 |
| CA2178033C true CA2178033C (en) | 2007-11-13 |
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ID=26307189
Family Applications (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002178032A Abandoned CA2178032A1 (en) | 1995-06-09 | 1996-06-03 | Glazing panel having solar screening properties |
| CA002178033A Expired - Lifetime CA2178033C (en) | 1995-06-09 | 1996-06-03 | Glazing panel having solar screening properties and a process for making such a panel |
Family Applications Before (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002178032A Abandoned CA2178032A1 (en) | 1995-06-09 | 1996-06-03 | Glazing panel having solar screening properties |
Country Status (17)
| Country | Link |
|---|---|
| JP (1) | JPH08337437A (en) |
| AT (1) | AT408978B (en) |
| BE (2) | BE1010321A5 (en) |
| CA (2) | CA2178032A1 (en) |
| CZ (2) | CZ290187B6 (en) |
| DE (2) | DE19622899B4 (en) |
| ES (2) | ES2126486B1 (en) |
| FR (2) | FR2735124B1 (en) |
| HU (1) | HU221059B1 (en) |
| IL (1) | IL118558A (en) |
| IT (2) | IT1285389B1 (en) |
| LU (1) | LU88767A1 (en) |
| NL (1) | NL1003294C2 (en) |
| PL (2) | PL179769B1 (en) |
| PT (1) | PT101879B (en) |
| SE (2) | SE514055C2 (en) |
| TR (1) | TR199600490A2 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH09169545A (en) * | 1995-12-21 | 1997-06-30 | Th Goldschmidt Ag | Method for pyrolytically forming layer comprising tin oxide doped with antimony oxide and lowering transmittance on glass or glass ceramic and composition therefor |
| US6124026A (en) * | 1997-07-07 | 2000-09-26 | Libbey-Owens-Ford Co. | Anti-reflective, reduced visible light transmitting coated glass article |
| US6218018B1 (en) * | 1998-08-21 | 2001-04-17 | Atofina Chemicals, Inc. | Solar control coated glass |
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| FR2899978A1 (en) * | 2006-04-14 | 2007-10-19 | Jacob Dahan | Screen e.g. LCD screen, masking device for e.g. flat screen TV, has glass faceplate with rear face including opaque cover made of black polyvinyl chloride and constituting opaque base of faceplate so as to transform faceplate into mirror |
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| JP6012887B2 (en) * | 2013-02-20 | 2016-10-25 | サン−ゴバン グラス フランス | Sheet glass with thermal radiation reflective coating |
| JP7283530B1 (en) * | 2021-12-28 | 2023-05-30 | Ａｇｃ株式会社 | Substrate with laminated film |
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| IT996924B (en) * | 1972-12-21 | 1975-12-10 | Glaverbel | PROCEDURE FOR FORMING A LAYER OF METALLIC OXIDE |
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-
1996
- 1996-06-03 CA CA002178032A patent/CA2178032A1/en not_active Abandoned
- 1996-06-03 CA CA002178033A patent/CA2178033C/en not_active Expired - Lifetime
- 1996-06-04 BE BE9600496A patent/BE1010321A5/en not_active IP Right Cessation
- 1996-06-04 IT IT96TO000479A patent/IT1285389B1/en active IP Right Grant
- 1996-06-04 BE BE9600497A patent/BE1010322A5/en active
- 1996-06-04 IL IL11855896A patent/IL118558A/en not_active IP Right Cessation
- 1996-06-04 JP JP8165370A patent/JPH08337437A/en active Pending
- 1996-06-04 IT IT96TO000478A patent/IT1285388B1/en active IP Right Grant
- 1996-06-05 LU LU88767A patent/LU88767A1/en unknown
- 1996-06-05 PT PT101879A patent/PT101879B/en not_active IP Right Cessation
- 1996-06-05 AT AT0097796A patent/AT408978B/en not_active IP Right Cessation
- 1996-06-06 FR FR9607035A patent/FR2735124B1/en not_active Expired - Lifetime
- 1996-06-06 ES ES009601248A patent/ES2126486B1/en not_active Expired - Fee Related
- 1996-06-06 ES ES009601249A patent/ES2126487B1/en not_active Expired - Fee Related
- 1996-06-06 FR FR9607034A patent/FR2735123B1/en not_active Expired - Lifetime
- 1996-06-07 SE SE9602269A patent/SE514055C2/en not_active IP Right Cessation
- 1996-06-07 HU HU9601586A patent/HU221059B1/en unknown
- 1996-06-07 PL PL96314663A patent/PL179769B1/en not_active IP Right Cessation
- 1996-06-07 DE DE19622899A patent/DE19622899B4/en not_active Expired - Lifetime
- 1996-06-07 TR TR96/00490A patent/TR199600490A2/en unknown
- 1996-06-07 NL NL1003294A patent/NL1003294C2/en not_active IP Right Cessation
- 1996-06-07 SE SE9602268A patent/SE513945C2/en not_active IP Right Cessation
- 1996-06-07 CZ CZ19961678A patent/CZ290187B6/en not_active IP Right Cessation
- 1996-06-07 PL PL96314664A patent/PL179768B1/en unknown
- 1996-06-07 DE DE19622898A patent/DE19622898B4/en not_active Expired - Lifetime
- 1996-06-07 CZ CZ19961679A patent/CZ295505B6/en not_active IP Right Cessation
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