NL9202186A - COATED GLASS. - Google Patents

Description

Lined glass

This invention relates to glass bearing a translucent multilayer coating.

Clad glass is used in a variety of areas for various purposes. The present invention mainly relates to the application of coatings to glass for sunscreen purposes.

The extensive architectural use of glazed facades imposes certain desiderata that the glass manufacturer must try to meet. From a technical point of view, it is often desirable that the glazing does not transmit too much of the total incident solar radiation in order to prevent the interior of the glazed structure from overheating during sunny weather. However, the glazing must also allow a fair amount of visible light to pass through to allow natural illumination of the interior of the structure and allow those present to look outside.

From an aesthetic point of view, it is sometimes preferable that the whole of a glazed facade of a building has an approximately uniform appearance: therefore it may be desirable that the windows of a building should be given certain reflex properties which, when viewed from the outside , are comparable to the opaque parts of the facade, such as window frames. Furthermore, it may be desirable to achieve a certain color for the coated glass when viewed in reflection.

According to the present invention, there is provided glass which bears a translucent multilayer coating, characterized in that the coating is successively: (A) a metal oxide layer (Mde A layer ") containing a material having a refractive index higher than that of the glass (B) a metal oxide or silica layer ("the B layer") which contains a material with a refractive index less than that of the A layer material; and (C) a layer ("the c layer") which contains a material selected from chromium, includes chromium-containing alloys, titanium aluminum alloys, nitrides thereof, and zirconium or titanium nitride.

The three coatings co-operate favorably for the purposes envisioned, and the precise properties obtained can be varied by varying the materials used and the thickness of these layers. The said third layer, the C layer of metal or nitride, is an absorbent layer, and it is mainly responsible for cutting off the transmission of the coated glass with respect to the total solar radiation. Increasing the thickness of that C-layer will decrease the total energy transmission and at the same time reduce the light transmission. This can also have an effect on the color of the glass when viewed in reflection. The said first two layers, the A and B layers with higher and lower refractive index respectively, can also change the light transmission properties of the coated glass. For a given thickness of the c-layer, they can be adjusted to increase the light transmittance and to increase the purity of the excitation color of reflected light. This can be done without reducing the total energy reflectivity of the coated glass; in fact, under certain circumstances, the reflectivity can be increased. Therefore, it is possible to reduce the absorption of radiant energy through the coated glass and to reduce its solar factor. We use the term "solar factor" to denote the sum of the directly transmitted total energy and the energy absorbed and radiated back on the other side of the energy source, as a share of the total radiant energy applied to the coated glass falls. Careful choice of the placement of the coatings on the glass relative to the observer and the thickness of such coatings may also allow to decrease the light reflector end power without increasing the 2 factor and / or a relatively neutral color. to gain.

It is considered a particularly important advantage that the use of a multilayer coating on glass according to the invention provides additional parameters (the materials and thicknesses of the layers) that can be changed to achieve a very good compromise between light transmission of the glass and its solar factor, and also that this makes it possible to obtain a degree of control over the color of the coated glass upon reflection. Therefore, the use of such coated glass in the facade of a building can also facilitate matching the exterior appearance of that facade between parts that are transparent and parts that are opaque.

The order of deposition of the three coatings on the glass, according to the invention, should be either A, B, C, or C, B, A. Which of these sequences is chosen depends on the manner in which the coated glass is applied in a building and on the desired optical properties. For example, the optical properties of a diamond coated in accordance with this invention may vary depending on whether the A layer or the C layer is closer to the observer.

In some preferred embodiments of the invention, the A layer is located between said C layer and the glass.

It is custom to define the various possible locations for a glass pane cladding as installed in an exterior window frame of a building in the following manner: position 1 is on the outside of the exterior or only the window pane and position 2 is the inside of that window; positions 3 and 4 are the outer and inner sides of the next window pane inside, if any, etc. In order to achieve the desired reflective aspect of the exterior of the building, the glass can be installed so that the A layer is between the C layer and the outside of the building. Therefore, such preferred embodiments of the invention wherein said A layer is interposed between said C layer can be positioned such that the cover layer is in position 2. Of course, a top layer formed by A, B and C layers deposited in the reverse order may also be in position 2. In either case, the coating is protected from exposure to prevailing weather conditions which could cause premature aging of the coating and deterioration of its properties. Further protection of the coating against premature aging due to atmospheric contaminants can be provided by incorporating such a coated glass pane into a hollow glazing panel with the coating on the inside of that panel. For example, contact between the cover layer and any atmospheric contaminants may be hindered or prevented if the interior of the hollow panel is closed.

Generally, when the C layer is made of chromium or nickel chromium, or a nitride of chromium, nickel chromium, zirconium or titanium, that layer can have atmospheric corrosion resistance that is adequate for all practical purposes. However, certain chromium-containing alloys such as stainless steels have less satisfactory resistance. Therefore, in some such preferred embodiments of the invention, said C-layer is a (chromium-containing) stainless steel layer which is again coated thereon with a protective layer of an oxide or nitride. There are a variety of oxide and nitride coatings which are known per se and which are hard and durable and thus contribute to the resistance of the coating as a whole to atmospheric corrosion and abrasion and thus resist premature aging of the coating.

When the C layer is made of a nitride, such as a titanium nitride, it can be protected by a thin layer of oxide. Therefore, in order to avoid scratching a titanium nitride layer, a fine coating of titanium oxide or tin oxide can be applied. These protective layers have little influence on the optical properties of the coating as a whole. For example, tin oxide is lightly lubricating and protects the coating against scratches. An oxide coating of less than 15 nm is suitable, such as 10 nm TiO2 or 15 nm SnO2.

In other preferred embodiments of the invention, said C layer is located between said A layer and the glass. A glass pane bearing such cladding can be installed as a window of a building with the cladding in position 1 to achieve the desired reflective aspect when viewed from outside the building. This will, admittedly, mean that the A layer of the cladding may have been exposed to prevailing weather conditions, but there are several high refractive index materials that can be easily deposited to form hard and durable cladding that have sufficient resistance to the intended purposes. atmospheric corrosion and attrition. A reverse-deposited coating could also be in position 1 so that the C-layer was exposed to prevailing weather conditions. Placing cladding in position 1 can have certain advantages from the viewpoint of filtering solar energy. Because the C layer of the cover absorbs the sun's rays, it will tend to get quite warm or even hot when exposed to strong sunlight. The load-bearing glass pane will also be heated. Consequently, the coated glass pane can become a source of a significant amount of infrared radiation. If the cladding is in position 1, there may be a slight tendency for such radiation to be emitted preferably to the outside of the building, but more importantly, the side of the clad glass occupying position 2 can be provided with a coating that reduces the radiation power of that side with regard to infrared radiation. For example, a doped tin oxide coating can be provided at position 2. This enhances the sunscreen effect of the coated glass.

It will be understood, of course, that such a low emissivity coating may advantageously be provided on a second pane of a hollow glazing panel which also includes a pane coated in accordance with this invention, whether that multilayer coating is position 1 or position 2 covers. Such a low emissivity coating would then occupy position 3 or position 4.

Preferably, such a C layer is of titanium nitride. Titanium nitride can also be formed into chemically and mechanically durable layers. In that layer, the titanium and nitrogen need not be present in stoichiometric proportions, indeed we have found that the best results are obtained when there is a stoichiometric excess of titanium, so that the layer may contain some free titanium. Such a layer can easily be formed by depositing titanium in the presence of nitrogen by cathode sputtering. The thickness of such a titanium nitride layer can be accurately reproducibly controlled by forming it in this way.

The thickness of such a C layer has a significant effect on the optical properties of the coated glass, in particular as regards its transmittance and its color in reflection. By varying the thickness of that coated layer, it is possible to achieve a variety of colors in reflection and a range of light transmittance. Preferably, such a zirconium or titanium nitride C layer has a geometric thickness in the range of 15 nm to 60 nm. Such layers tend to have a blue to greenish hue in reflection. Other materials suitable for forming the said c-layer, namely chromium, chromium-containing alloys and nitrides thereof, can be formed into layers of coatings which have a neutral or gray hue in reflection. The use of titanium-aluminum alloys or nitrides thereof allows the formation of a wide range of coating colors.

Since said C-layer absorbs the incident radiation quite and can become quite hot, the glass could be exposed to a degree of thermal shock that would be unacceptable for safety reasons unless the glass types were reinforced in any way. The glass is therefore advantageously tempered glass. The annealing treatment used may be a thermal annealing treatment or a chemical annealing treatment. In certain cases (such as when the light transmittance is high - on the order of 40%) - the reduction of the solar factor resulting from certain embodiments of the invention allows the need for mechanical reinforcement of the glass by means of avoid tempering or hardening. Namely, the modification of the selectivity reduces the absorption in the coating for a given light transmission and therefore also reduces the heating effect on the glass.

Preferably said A layer, the layer with a higher refractive index, is a layer consisting essentially of titanium dioxide, zirconia and / or tin dioxide. A suitable titanium dioxide layer can be formed with a refractive index of about 2.3 by a cathode sputtering technique known per se. Zirconia has a refractive index of 2.1. A tin dioxide coating can be formed in a similar manner, again with a refractive index near 2. Both of these materials can be formed into high quality layers that are transparent and chemically and mechanically durable.

Rather, it may be preferable to pyrolytically deposit one or more such coatings to promote abrasion and corrosion resistance. It is currently envisioned that such a pyrolytically deposited coating is formed either directly on the glass or on a pre-deposited pyrolytic coating.

Advantageously, the said A layer has an optical thickness in the range from 20 nm to 190 nm and preferably in the range from 30 nm to 100 nm. The effect that the A layer has on the radiant energy transmission properties of the coated glass is therefore enhanced due to interference effects.

Preferably, the B layer is the lower refractive index layer, a layer consisting mainly of silicon oxide. The use of silicon oxide is favorable because it can also be formed into chemically and mechanically durable layers. A suitable silicon oxide layer can be formed by cathode sputtering. Such cathode sputtering can be performed in the presence of oxygen in such an amount that the oxygen content of the layer that is formed is regulated so that that layer has the lowest refractive index as desired. For example, it is possible to obtain a silicon oxide layer with a refractive index of about 1.4 to 1.45.

Advantageously, said B layer has an optical thickness in the range from 5 nm to 120 nm, and preferably in the range from 5 to 60 nm, and most preferably from 14 nm to 60 nm. The effect that the layer has on the radiation energy transmission properties of the coated glass is thereby also enhanced due to interference effects.

Certain preferred embodiments of the invention will now be described, by way of example, in further detail and with reference to the accompanying schematic drawings in which: Figures 1 to 3 are each a detail and a schematic cross section of an embodiment of a glass panel according to this invention.

In Figure 1, a glass pane G1 is successively coated with an A-layer, a B-layer and a C-layer which together form a multi-layered cladding at position 2, ie on the inside of the outer or only pane of a window . The glass pane G1 is optionally combined with a second glass pane G2 to form a hollow panel unit which may be hermetically sealed to protect the trim A, B, C from contact with ambient air. Such an optional second glass pane G2 is shown carrying an optional coating E at position 3 of a material adapted to reduce the emissivity of the position 3 side of the glass pane G with respect to infrared radiation. Since the emissivity is reduced, the reflectivity is increased so that infrared radiation emitted from the first coated glass pane G1 is radiated back to the outside of the building. As a variant, such an optional cover E can be applied with a similar result to the position 4 side of the glass pane G2, although in this case the second pane G2 will tend to become hotter than if that cover E was in position 3 .

In Figure 2, a glass pane G is successively coated with a C-layer, a B-layer and an A-layer which together form a multilayer cladding at position 1. Any cladding E is also provided on the glass pane G at position 2 and consists of a material adapted to reduce the radiation power of the position 2 side of the glass pane G with respect to infrared radiation.

In Figure 3, a glass pane G3 is successively coated with an A-layer, a B-layer and a C-layer which together form a multi-layered cladding at position 2, ie on the inside of the outer or only pane of a window. The glass pane G is shown carrying an optional coating P, also at position 2, of an oxide or nitride whose purpose is to increase the resistance of the C layer to chemical and / or physical attack.

EXAMPLE I

A 6 mm thick ribbon of float glass was passed through a coating station while still hot after leaving a float chamber, and a tin dioxide coating was formed on the glass by pyrolysis in a manner known per se, to form a optical thickness between 30 and 100 mm to serve as an A layer. The tape was cut into diamonds and the diamonds were then thermally tempered. In one variant, the glass panes were pyrolytically coated before cutting, and after such coating, the cooling schedule was drawn up such that such panes were thermally tempered.

A tempered pyrolytic-coated glass pane was placed in a processing chamber containing two planar magnetron-cathode sputtering sources targeting titanium and silicon, respectively, and provided with inlet and outlet gas locks, a substrate conveyor, power sources, cathode atomizing gas inlets and an exhaust outlet.

The pressure in the chamber was lowered to 0.15 Pa. The substrate was transported past the cathode sputtering sources with the silicon source activated, and cold cathode sputtering with oxygen gas occurred at an effective deposition pressure of 0.2 Pa to yield a silicon oxide layer (a B layer) with a refractive index of 1.4 and an optical thickness between 10 and 120 nm, after which the silicon source was deactivated. In a variant, the silicon source consisted of a rotating cathode.

Oxygen was purged from the system and nitrogen was introduced as cathode sputtering gas at a pressure of 0.3 Pa. The titanium source was activated and the substrate was transported past it to deposit a layer comprising titanium nitride with a geometric thickness between 15 and 60 nm. In fact, after later analysis, this "titanium nitride" layer was found to contain a slight stoichiometric excess of titanium.

EXAMPLE II

A 6 mm thick alkali-lime glass pane of ordinary composition was chemically tempered. The chemical annealing was performed by contacting the glass with molten potassium nitrate at a temperature of 465 ° C for between 2½ hours and 8 hours to achieve the desired degree of compressive surface loading of 450 to 600 MPa in the surface of the glass. The glass was float glass, and prior to tempering, it was held at a temperature of 465 ° C for a period of 8 hours to restore the equilibrium of the ion populations of opposing surface layers of the glass. In a variant, the glass used was drawn glass with a thickness of 4 mm, and this pretreatment was omitted.

Three coatings A, B and C of titanium dioxide, silicon oxide and titanium nitride, respectively, were applied to the glass. In order to deposit these layers, the substrate was placed in a processing chamber containing two planar magnetron cathode sputtering sources targeting titanium and silicon, respectively, and provided with inlet and outlet gas locks, a conveyor belt for the substrate, power sources, sputtering gas inlets and an exhaust outlet.

The pressure in the chamber was lowered to 0.15 Pa. The substrate was transported through the sputtering sources with the titanium source activated and cold cathode sputtering with oxygen gas in the presence of argon at an effective deposition pressure of 0.2 Pa to yield a titanium dioxide layer with a refractive index of 2.3. The titanium source was deactivated and the silicon source was activated, and the substrate was transported back through that source to deposit a silicon oxide layer with a refractive index of 1.4, after which the silicon source was deactivated.

In a variant, the silicon source consisted of a rotating cathode. In a further variant, the titanium and silicon sources were activated simultaneously and the substrate was transported along it for the subsequent deposition of the two coatings. Finally, oxygen was purged from the system and nitrogen was introduced at a pressure of 0.3 Pa as a sputtering gas. The titanium source was reactivated and the substrate was transported along it to deposit a layer comprising titanium nitride with a geometric thickness between 15 nm and 60 nm. In fact, this "titanium nitride" layer was found to contain a slight stoichiometric excess of titanium upon closer analysis.

The thickness of these three coatings was as follows: Layer A - titanium dioxide - geometric thickness 35 nm. Layer B - silicon oxide - geometric thickness 20 nm. Layer C - titanium nitride - geometric thickness 35 nm. The result was a glass pane bearing successively deposited coatings A, B and C as shown in Figures 1 and 3 of the drawings.

The optical properties of the coated pane when in position 2 as viewed from the glass side were light transmission - 25% light reflection <10%.

The reflected color was purple with a purity of more than 40%.

EXAMPLES III AND IV

In variants of Example II, the three coatings were deposited in the same order, namely, with the titanium oxide coating adjoining the glass, but of different thicknesses. The geometric thicknesses and properties of the different panes are given in the following table 1, the panes being coated in position 2 and examined from the glass side: TABLE 1

Ex. III Ex. IV

TiO 2 thickness 25 nm 20 nm

Thickness SiO2 40 nm 10 nm

Thickness TiN 25 nm 25 nm

Light transmission 30% 30%

Light reflection 9% 8%

Solar factor 39% 39%

Tint violet-purple neutral

Predominant wavelength 470 nm

Color purity 44% 3%

Hunter coordinate a +7

Hunter coordinate b -29

It should be noted that the coated pane of Example IV has a light reflection and color close to that of uncoated glass, but with a relatively low solar factor.

EXAMPLE V

In a variant of Example II, the three coatings of the same thickness were deposited, but in reverse order on one side of a glass pane.

The thus coated pane provided a solar factor of 34% with the uncoated side toward the energy source and had the following optical properties when viewed from the uncoated side:

Light reflection = 28%

Light transmission T_ = 30%

Li

Hunter coordinates a = 0, b = 14

Tint in reflection: golden yellow with a predominant wavelength at 575 nm and a color excitation purity of 28%.

In order to achieve the same 30% light transmission using only a titanium nitride coating on the glass, that coating could be formed in the same manner but at a thickness of 23 nm, and would provide a light reflection of 13%. However, its solar factor would be 38%, and the hue would be blue with an excitation color purity of 19%. Therefore, by adopting this example of the invention, the solar factor and the ratio of light transmission to solar factor are improved and the color changed.

Similarly, if a single titanium nitride coating with the same thickness of 35 nm was formed, the light transmission would be reduced to only 20% with a light reflection of 20% and a solar factor of 31%. Also, the shade would be blue, but with a color excitation purity of 13%. Again the ratio of the light transmission to the solar factor was improved and the color changed.

In a variant of this example, the other side of the glass pane carried a low emissivity pyrolytically formed coating on the other side thereof, resulting in a coated pane as shown in Figure 2 of the drawings.

EXAMPLES VI TO VIII

In variants of Example V, the three coatings were deposited in the same order, namely that the titanium nitride is adjacent to the glass, but of different thicknesses. Those geometric thicknesses and the properties of the different coated panes are given in the following Table 2, along with comparative examples cf. A and c. B. The solar factor was measured with the uncoated side of the glass towards the energy source, and the optical properties are viewed from the uncoated side of the glass pane.

TABLE · 2

vb.vi vv.vu vb.vin Cf.A cf. B.

Thickness TiN 50 nm 20 nm 20 nm 15 nm 35 ni

Thickness Si02 25 nm 35 nm 15 nm -0- -0-

Thickness Ti02 20 nm 35 nm 15 nm -0- -0-

Light transmission 20% 40% 40% 40% 20%

Light reflection 25% 23% 22% 8% 20%

Solar factor 28% 43% 42% 47% 31%

Tint golden yellow golden yellow blue blue blue

Predominant 576 nm 576 nm 482 nm 478 nm 478 nm wavelength

Color purity 21% 37% 19% 21% 13%

Hunter coordinate a 0 0 -3.5 0 -2

Hunter coordinate b +10.5 +16 +11 -8.5 -7

EXAMPLES IX TO XII

In variants of Example II, the processing chamber contained an extraplanar magnetron sputtering source which was activated to deposit a layer c with a geometric thickness of between 15 nm and 60 nm.

In Example 9, that additional source was stainless steel, and that source was activated in an argon atmosphere at a pressure of 0.3 Pa. for forming a translucent layer C of stainless steel. In this example, the stainless steel layer was the first layer deposited on the glass pane.

The thicknesses of the three coating layers were as follows: Layer C - stainless steel - geometric thickness 5 nm Layer B - silicon oxide - geometric thickness 30 nm Layer A - titanium dioxide - geometric thickness 30 nm. The window thus coated provided a solar factor of 53% with its uncoated side toward the energy source and had the following optical properties when viewed from the uncoated side:

Light reflection = 33%

Light transmission TT = 48% ij

Tint in reflection: yellowish gray with a color ex citation purity of 7%.

Such a coated pane could be compared to a pane bearing a two-layer coating of stainless steel (5 nm) and titanium dioxide (10 nm), which provided a more or less comparable solar factor of, to be precise, 51% . Such a pane had the following optical properties when viewed from the uncoated side:

Light reflection = 13%

Light transmission T_ = 37%

Ij

Tint in reflection: bluish gray with a color ex citation purity of 10%.

In a variant of Example 9, stainless steel was deposited by sputtering in the presence of nitrogen at a pressure of 0.3 Pa to form a "stainless steel nitride" coating. This had no great effect on the energy transmission properties of the coated glass pane, but it was noted that the corrosion resistance of the coating was improved.

In Example 10, the additional source was chromium, and that source was activated in an argon atmosphere at a pressure of 0.3 Pa to form a translucent chromium layer C. In a variant of Example 10, the chromium was applied in the presence by sputtering of nitrogen at a pressure of 0.3 Pa to form a chromium nitride coating.

In Example 11, that additional source was a nickel chromium alloy, and that source was activated in an argon atmosphere at a pressure of 0.3 Pa to form a translucent layer C of nickel chromium alloy. In a variant of Example 11, the nickel chromium alloy was sputter applied in the presence of nitrogen at a pressure of 0.3 Pa to form a "nickel chromium nitride" coating layer. In a further variant of Example 11, zirconium was sputter deposited in the presence of nitrogen at a pressure of 0.3 Pa to form a zirconium nitride layer.

In Example 12, that additional source was a titanium aluminum alloy, and that source was activated in an argon atmosphere at a pressure of 0.3 Pa to form a translucent layer C of titanium aluminum alloy. In a variant of Example 12, the titanium aluminum alloy was applied by sputtering in the presence of nitrogen at a pressure of 0.3 Pa to form a "titanium aluminum nitride" coating,

EXAMPLE XIII

In a variant, four coatings were deposited with a titanium oxide coating adjacent to the glass.

The thicknesses and materials of the four coatings were as follows:

Layer A - titanium dioxide - geometric thickness 20 nm.

Layer B - silicon oxide - geometric thickness 20 nm

Layer C - stainless steel - geometric thickness 6 nm, and - titanium nitride - geometric thickness 15 nm.

The thus coated pane provided a solar factor of 29% from the coated side, and had the following optical properties when viewed from the coated side:

Light reflection = 44%

Light transmission TL = 23%

Tint in reflection: no discernible. The glass had an excitation purity of 1%.

EXAMPLES XIV AND XV

In variants of Example V, the three coating coatings were deposited in the same order, namely with the titanium nitride adjacent to the glass. Those geometric thicknesses and the properties of the various coated panes are shown in the following Table 3, with the optical properties viewed from the coated side.

TABLE 3

Ex.XIV Ex.XV Cf. A Cf. B

Thickness TiN 35 nm 35 nm 15 nm 35 nm

Thickness Si02 20 nm 40 nm -0- -0-

Thickness Ti02 3 5 nm 40 nm -0- -0-

Light transmission 30% 20% 40% 20%

Light reflection 5% 35% 22% 35%

Solar factor 36% 33% 42% 26%

Tint purple blue blue blue green

Color purity 76% 32% 10% 5%

Predominant 470 nm 478 nm 478 nm 481 nm wavelength

Hunter coordinate a +17 -200

Hunter coordinate b -65 -30 -7 -3.5

EXAMPLES XVI TO XX

The further examples in Table 4 below were prepared in the same manner as described in connection with Example V, except that in Examples XVIII and XIX, the coatings were deposited by pyrolysis using the method well known in the art, rather than using sputtering.

TABLE 4

Ex.XVI Ex.XVII Ex.XVII Ex.XIX Ex.XX

Thickness:

TiO2 (A) 55 nm 25 m 3 0 nm 20 nm 10 nm

SiO2 (B) 30 nm 10 nm 70 nm 80 nm 60 nm

TiN (C) 23 nm 35 nm 23 nm 23 nm 15 nm

Cladding order CBA ABC ABC CBA ABC

Viewed silk glass glass glass coating coating

Light transmission 28% 24% 26% 31% 42%

Light reflection 17% 7% 26% 27% 22%

Solar factor 39% 35% 37% 40% 43%

Tint gold color. neutral blue blue neutral

Predominant 589 nm - 477 nm 477 nm - wavelength

Purity 33% 1% 32% 36% 1%

Hunter coordinate a +10 0 -0.5

Hunter coordinate b +11.5 -26 -31.4

Claims (13)

Glass bearing a multilayer translucent coating, characterized in that the coating successively comprises: (A) a metal oxide layer ("the A layer") containing a material having a refractive index higher than that of the glass; (B) a metal oxide or silica layer ("the B layer") containing a material with a lower refractive index than that of the material of the A layer; and (C) a layer ("the c-layer") containing a material selected from chromium, chromium-containing alloys, titanium aluminum alloys, nitrides thereof, and zirconium or titanium nitride. Coated glass according to claim 1, characterized in that said A layer is located between said c layer and the glass. Coated glass according to claim 2, characterized in that said C-layer is a (chromium-containing) stainless steel layer which in turn is coated with a protective coating of an oxide or nitride. Coated glass according to claim 1, characterized in that said C-layer is located between said A-layer and the glass. Coated glass according to any one of claims 1, 2 and 4, characterized in that said C-layer is titanium nitride. Coated glass according to claim 5, characterized in that said C-layer has a geometric thickness in the range from 15 nm to 60 nm. Coated glass according to any one of the preceding claims, characterized in that said glass is tempered glass. Coated glass according to any one of the preceding claims, characterized in that said A layer is a layer consisting essentially of titanium dioxide, zirconium dioxide and / or tin dioxide. Coated glass according to any one of the preceding claims, characterized in that said A layer has an optical thickness in the range from 20 nm to 190 nm. Coated glass according to any one of the preceding claims, characterized in that said A layer has an optical thickness in the range from 30 nm to 100 nm. Coated glass according to any one of the preceding claims, characterized in that said B layer is a layer mainly consisting of silicon oxide. Coated glass according to any one of the preceding claims, characterized in that said B layer has an optical thickness in the range from 5 nm to 120 nm. Coated glass according to claim 12, characterized in that said B layer has an optical thickness in the range from 14 nm to 60 nm.