Glass sheet and method for producing glass sheet

Abstract

The glass sheet of the present invention is a glass sheet with a thickness of 1.6 mm or less produced by a float process in which a molten glass material is formed into a sheet on a molten metal. When one surface of the glass sheet kept in contact with the molten metal during the formation of the molten glass material into the glass sheet is defined as a first surface and the other surface of the glass sheet opposite to the first surface is defined as a second surface, at least the first surface has been subjected to a treatment for forming a densified dealkalized layer therein. An etching rate ER.sub.1 (nm/min) of the first surface and an etching rate ER.sub.2 (nm/min) of the second surface satisfy a relation of ER.sub.2/ER.sub.10.8 when the first surface and the second surface are etched using 0.1 mass % hydrofluoric acid at 50 C. as an etching liquid.

Claims

1. A glass sheet with a thickness of 1.6 mm or less produced by a float process in which a molten glass material is formed into a sheet on a molten metal, wherein when one surface of the glass sheet kept in contact with the molten metal during the formation of the molten glass material into the glass sheet is defined as a first surface and the other surface of the glass sheet opposite to the first surface is defined as a second surface, at least the first surface has been subjected to a single treatment for forming a densified dealkalized layer therein at a treatment temperature at or within a range of 410 C. to 580 C., and an etching rate ER.sub.1 (nm/min) of the first surface and an etching rate ER.sub.2 (nm/min) of the second surface satisfy a relation of ER.sub.2/ER.sub.10.8 when the first surface and the second surface are etched using 0.1 mass % hydrofluoric acid at 50 C. as an etching liquid, and the etching rate ER.sub.1 is 10 nm/min or more.

2. The glass sheet according to claim 1, wherein ER.sub.1 and ER.sub.2 satisfy a relation of ER.sub.2/ER.sub.10.7.

3. The glass sheet according to claim 2, wherein the second surface has been subjected to a treatment for forming a densified dealkalized layer therein.

4. The glass sheet according to claim 1, wherein the second surface has been subjected to a treatment for forming a densified dealkalized layer therein.

5. A method for producing a glass sheet with a thickness of 1.6 mm or less, comprising the steps of: (I) forming a molten glass material into a glass ribbon on a molten metal; and (II) subjecting at least one surface of the glass ribbon kept in contact with the molten metal in the step (I) to a single treatment for forming a densified dealkalized layer therein at a treatment temperature at or within a range of 410 C. to 580 C. so that an etching rate ER.sub.1 (nm/min) of the one surface of the glass ribbon defined as a first surface and an etching rate ER.sub.2 (nm/min) of the other surface of the glass ribbon defined as a second surface opposite to the first surface satisfy a relation of ER.sub.2/ER.sub.10.8 when the first surface and the second surface are etched using 0.1 mass % hydrofluoric acid at 50 C. as an etching liquid, wherein the treatment temperature for a portion of the treatment for forming the densified dealkalized layer is less than 500 C.

6. The method for producing a glass sheet according to claim 5, further comprising, after the step (II), a step of (III) subjecting a glass sheet obtained by cutting the glass ribbon to chemical strengthening by alkali ion exchange.

Description

BRIEF DESCRIPTION OF DRAWINGS

(1) FIG. 1 is a schematic diagram showing an example of a system capable of carrying out the production method of the present invention.

DESCRIPTION OF EMBODIMENTS

(2) Hereinafter, an embodiment of the present invention will be described in detail.

(3) A glass sheet of the present embodiment is a glass sheet produced by a float process, which is a continuous glass sheet production method. In the float process, a glass material is melted in a float furnace and the molten glass material is formed into a sheet-shaped glass ribbon on a molten metal in a float bath. The glass ribbon thus obtained is annealed in an annealing furnace and then cut into glass sheets of a predetermined size. In the present embodiment, the case where molten tin is used as the molten metal is described. Hereinafter, one surface of a glass sheet kept in contact with molten tin in a float bath in the forming step is referred to as a bottom surface (first surface), while the other surface of the glass sheet kept out of contact with the molten tin is referred to as a top surface (second surface) opposite to the bottom surface.

(4) Furthermore, in the glass sheet of the present embodiment, at least the bottom surface thereof has been subjected to dealkalization for forming a damage-preventing protective coating thereon and a subsequent treatment for forming a densified layer. As used herein, dealkalization refers to a treatment for bringing an alkali-reactive oxidizing gas into contact with the surface of the glass sheet so as to remove an alkali component from the glass. The removed alkali component reacts with the oxidizing gas, and as a result, a protective coating is formed on the surface of the glass sheet.

(5) Instead of the alkali component removed from the glass by dealkalization, atmospheric water in various forms, such as in the form of proton (H.sup.+) and oxonium ion (H.sub.3O.sup.+), enters the glass and forms a silanol group (SiOH) in the dealkalized layer. Then, a siloxane bond (SiOSi) is formed by dehydration condensation of the silanol group. In this description, densification is defined as the state in which siloxane bonds are increased by this dehydration condensation. Since the glass surface having increased siloxane bonds is more resistant to etching, the degree of densification can be obtained by measuring the etching rate.

(6) As an oxidizing gas, for example, sulfur dioxide (SO.sub.2) gas can be used. SO.sub.2 reacts with a component of the glass and forms alkali sulfate such as sodium sulfate on the surface of the glass sheet. This alkali sulfate serves as a protective coating. The oxidizing gas used herein may be a gas other than SO.sub.2 gas as long as the gas can react with an alkali component in the glass to form a protective coating. It is not desirable to use a very effective dealkalizing gas such as hydrogen fluoride gas because not only it is not involved in forming a protective coating but also it etches the glass surface to make the surface rough. An inert gas such as air, nitrogen, or argon may be used as a carrier gas. The oxidizing gas may further contain water vapor.

(7) The top surface also may be subjected to a treatment for forming a densified dealkalized layer. Even if SO.sub.2 is blown only to the bottom surface, a portion of the blown SO.sub.2 gas may move around to the top surface and treat the top surface.

(8) In the glass sheet of the present invention, the etching rate ER.sub.1 (nm/min) of the bottom surface and the etching rate ER.sub.2 (nm/min) of the top surface satisfy a relation of ER.sub.2/ER.sub.10.8 when the bottom surface and the top surface are etched using 0.1 mass % hydrofluoric acid at 50 C. as an etching liquid. Since the bottom surface has been kept in contact with molten tin in the float bath, tin enters the glass through the bottom surface and a tin layer is formed therein. A layer densified by dehydration condensation through dealkalization is also formed in the bottom surface. The etching rate ER.sub.1 of the bottom surface is determined by the altered layer composed of the tin layer and the densified layer. A layer densified by dehydration condensation through dealkalization may also be formed in the top surface, and in this case, the etching rate ER.sub.2 of the top surface is determined by the layer densified by dehydration condensation through dealkalization and the like. Therefore, the etching rates ER.sub.1 and ER.sub.2 satisfying ER.sub.2/ER.sub.10.8 can be obtained by controlling the densified layers formed in the bottom surface and the top surface, that is, by controlling the degrees of densification by dealkalization of the bottom surface and the top surface.

(9) The degrees of densification by dealkalization of the bottom surface and the top surface can be controlled by the amount of blown SO.sub.2 gas, the surface(s) to which SO.sub.2 gas is blown (only the bottom surface or both the bottom surface and the top surface), the temperature of dealkalization, etc. Densification is less likely to occur even if dealkalization is performed at a relatively low temperature. In the case of common soda lime glass, densification is more likely to occur when SO.sub.2 gas is allowed to act on the glass at a temperature of about 500 C. or more. In order to form as much protective coating as possible without promoting densification so much, it is desirable to minimize the duration of action of SO.sub.2 gas at 500 C. or more and to maximize the duration of action of SO.sub.2 gas at lower temperatures (for example, less than 500 C.).

(10) The tin layer in the bottom surface can be a factor that increases the etching rate. On the other hand, since the densified layer is more resistant to etching, it can be a factor that reduces the etching rate. Therefore, two phenomena, i.e., an increase in the etching rate by the tin layer and a decrease in the etching rate by the densified dealkalized layer, occur simultaneously in the bottom surface. On the other hand, the etching rate of the top surface depends on the densified dealkalized layer. Since the bottom surface is usually more susceptible to damage than the top surface, the amount of SO.sub.2 acting on the bottom surface tends to be increased to form more protective coating. This leads to the predictable result that in conventional glass sheets, the etching rate of the bottom surface is comparable to or lower than the etching rate of the top surface even if the effect of the tin layer is added. In the glass sheet of the present embodiment, ER.sub.2/ER.sub.1 is 0.8 or less, which means that the degree of densification of the bottom surface is relatively low. The ratio ER.sub.2/ER.sub.1 of 0.8 or less makes it possible to achieve a good balance between alkali ion exchange in the top surface and that in the bottom surface and thus to reduce warping after chemical strengthening. Since warping after chemical strengthening can be reduced when ER.sub.1 and ER.sub.2 satisfies the relation of ER.sub.2/ER.sub.10.8, the values of ER.sub.1 and ER.sub.2 are not particularly limited.

(11) It is desirable that ER.sub.1 and ER.sub.2 satisfy a relation of ER.sub.2/ER.sub.10.7. This ratio ER.sub.2/ER.sub.1 of 0.7 or less makes it possible to further reduce the amount of warping after chemical strengthening. It is possible, for example, to reduce the amount of warping of a glass sheet after chemical strengthening to 0.1% or less of the long side dimension of the glass sheet. In order to further reduce the amount of warping after chemical strengthening, it is more desirable that ER.sub.1 and ER.sub.2 satisfy a relation of ER.sub.2/ER.sub.10.4. In order to achieve a good balance of alkali ion exchange, ER.sub.2/ER.sub.1 is desirably 0.05 or more, and more desirably 0.1 or more.

(12) Soda lime glass or aluminosilicate glass, which is commonly available for use as glass for chemical strengthening, can be used for the glass sheet, and the composition of the glass is not particularly limited. A thin glass sheet with a thickness of 1.6 mm or less is particularly susceptible to warping by chemical strengthening. Therefore, the thickness of the glass sheet of the present embodiment is 1.6 mm or less. In particular, when the present invention is applied to a thin glass sheet with a thickness of 1.1 mm or less, remarkable effects can be obtained.

(13) The glass sheet of the present embodiment can be produced, for example, by a method including the steps of: (I) forming a molten glass material into a glass ribbon on molten tin (molten metal); and (II) subjecting at least one surface of the glass ribbon kept in contact with the molten tin in the step (I) to a treatment for forming a densified dealkalized layer therein so that an etching rate ER.sub.1 (nm/min) of the one surface of the glass ribbon defined as a first surface and an etching rate ER.sub.2 (nm/min) of the other surface of the glass ribbon defined as a second surface opposite to the first surface satisfy a relation of ER.sub.2/ER.sub.10.8 when the first surface and the second surface are etched using 0.1 mass % hydrofluoric acid at 50 C. as an etching liquid. This method can be carried out, for example, using a system shown in FIG. 1.

(14) First, a glass material is melted in a float furnace 11. Molten glass 14 flowing from the float furnace 11 is fed into a float bath 12. The molten glass 14 thus fed into the float bath 12 is formed into a sheet-like glass ribbon 16 while spreading over molten tin 15 having a higher specific gravity than the glass in the float bath 12. As the glass flows along the float bath 12, the thickness of this glass ribbon 16 is adjusted and the glass ribbon 16 is cooled to provide a viscosity high enough to be pulled out of the bath 12. The cooled glass ribbon 16 is lifted off the float bath 12 and delivered to an annealing furnace 13. The annealing furnace 13 is provided with gas blowing nozzles 17 for dealkalization. The nozzles 17 are provided on both surface sides of the glass ribbon 16 so that gas can be blown onto both surfaces of the glass ribbon 16. The amount of the gas blown from the gas blowing nozzles 17 can be controlled by a controller (not shown). The annealing furnace 13 is further provided with a heating means and a cooling means (not shown), and thereby the dealkalization temperature can be set within a predetermined range. Thus, in the annealing furnace 13, the glass ribbon 16 is subjected to a treatment for forming a densified dealkalized layer therein at an appropriately adjusted treatment temperature and with an appropriately adjusted amount of blown SO.sub.2 gas, so that ER.sub.1 and ER.sub.2 satisfy the relation of ER.sub.2/ER.sub.10.8. Thereafter, the glass ribbon 16 is cut into glass sheets of a predetermined size.

(15) In order to chemically strengthen the glass sheet of the present embodiment, it is desirable to further carry out, after the step (II), a step of (III) subjecting a glass sheet obtained by cutting the glass ribbon to chemical strengthening by alkali ion exchange. The amount of warping of the chemically strengthened glass sheet obtained by this step is reduced to a lower level, and thus this glass sheet has both high flatness and high strength.

EXAMPLES

(16) Hereinafter, the present invention is described in more detail using examples. However, the present invention is not limited to the following examples, and other examples are possible as long as they do not depart from the gist of the present invention.

Examples 1 to 6

(17) [Method for Producing Glass Sheet]

(18) Glass sheets with a thickness of 0.33 mm were produced by a float process. First, a glass material was prepared so as to have the following composition of glass: 71.5% of SiO.sub.2, 1.7% of Al.sub.2O.sub.3, 8% of CaO, 4% of MgO, 13.6% of Na.sub.2O, 0.9% of K.sub.2O, 0.2% of SO.sub.2, and 0.1% of total iron (in terms of Fe.sub.2O.sub.3), where % means mass %. This glass material was melted, and the molten glass material was formed into a sheet shape on molten tin in a float bath. Thereafter, in an annealing furnace, the bottom surface of the glass sheet was subjected to a treatment for forming a densified dealkalized layer therein by blowing SO.sub.2 gas onto the bottom surface thereof. The SO.sub.2 gas was blown only to the bottom surface, but a portion of the SO.sub.2 gas moved around to the top surface, and the top surface also was subjected to the same treatment. Table 1 shows the amount of blown SO.sub.2 gas in each example. Table 1 also shows the temperature at which the SO.sub.2 gas was blown, i.e., the treatment temperature, in each example.

(19) [Method for Measuring Etching Rate]

(20) The etching rate of the glass sheet obtained was evaluated based on the etching rate calculated from the etching amount obtained by immersing the glass sheet in 0.1 mass % hydrofluoric acid at 50 C. as an etching liquid for 3 minutes. The etching amount was measured by applying a hydrofluoric acid-resistant masking agent onto a portion of the unetched glass sheet, subjecting the glass sheet to etching, and measuring the difference in the level between the masked portion and the etched portion formed by etching. The level difference was measured using a thickness meter (Alpha-Step 500 manufactured by KLA-Tencor Corporation). Table 1 shows the measurement results of the etching rates (ER.sub.1 and ER.sub.2) and the etching rate ratios (ER.sub.2/ER.sub.1) obtained from these measurement results. Here, the etching time (3 minutes) was set so that only the etching rate of the altered layer formed in the surface of the glass sheet could be measured independently of the etching rate of the bulk layer inside the glass sheet. Specifically, a plurality of data of changes in the etching rate with respect to the etching time were collected, and the etching depth was plotted on the vertical axis while the time was plotted on the horizontal axis. When the plots were connected, a straight line having a gentle slope was observed between the plots in a short time region, while a straight line having a steeper slope was observed between the plots in a longer time region. Thus, a bending point was observed between the lines. It was presumed that the etching depth at which this bending point was observed was the depth at which the composition of the altered layer changed to that of the bulk layer. Therefore, in this case, the etching time (3 minutes in this case) was selected so that the etching depth did not reach the bulk layer.

(21) [Method for Chemical Strengthening]

(22) A sample having a size of 370 mm470 mm and a sample having a size of 50 mm50 mm were cut out from each glass sheet. These samples were subjected to chemical strengthening. First, these samples were washed, and then immersed in a molten salt of KNO.sub.3. The temperature of the molten salt of KNO.sub.3 was set to 460 C., and the immersion time was set to 30 minutes. The samples were taken out from the molten salt of KNO.sub.3 and then cooled, followed by washing to remove KNO.sub.3 attached to the samples.

(23) [Method for Measuring Amount of Warping]

(24) As for the sample having a size of 370 mm470 mm, the chemically strengthened one was placed on a flat surface plate in such a manner that the convex-warped top surface thereof faced downward, and the distances at eight points between the sample and the surface plate were measured using a gap gauge. The maximum value of the distance was used as the amount of warping. Table 1 shows the results.

(25) As for the sample having a size of 50 mm50 mm, two opposite lateral sides of the chemically strengthened one were supported in such a manner that the convex-warped top surface faced upward, and the height-direction coordinate of the center of the top surface was measured. Next, the sample was turned over, and the height-direction coordinate of the center of the top surface was measured in the same manner. One half of the sum of the two measurement values was used as the amount of warping. For the measurement of the coordinates, a non-contact three-dimensional profile measurement system (NH-3N manufactured by Mitaka Kohki Co., Ltd.) was used. The effect of deformation of each sample under its own weight was eliminated from the amount of warping thus obtained by performing the above-described measurement on both the top surface and the bottom surface. Table 1 shows the results.

Comparative Examples 1 to 3

(26) Glass sheets were produced in the same manner as in Examples 1 to 6 except that the treatment was performed with the amounts of blown SO.sub.2 gas and at the treatment temperatures as shown in Table 1. For each of the glass sheets obtained, the etching rate was measured, chemical strengthening was performed, and the amount of warping was measured in the same manner as in Examples 1 to 6. Table 1 shows the results.

(27) TABLE-US-00001 TABLE 1 Examples Comparative Examples 1 2 3 4 5 6 1 2 3 Etching rate of bottom 10 10 11 11 12 11 7 8 5 surface: ER.sub.1 (nm/min) Etching rate of top 8 8 6 8 7 7 8 7 5 surface: ER.sub.2 (nm/min) ER.sub.2/ER.sub.1 0.8 0.8 0.6 0.7 0.5 0.6 1.1 0.9 1.0 Amount of warping of 0.83 0.68 0.48 0.47 0.5 0.52 1.28 1.23 1.46 chemically strengthened 370 mm 470 mm sample (mm) Amount of warping of 62.8 68.8 54.5 44.7 57.5 57.5 69.2 69.5 84.2 chemically strengthened 50 mm 50 mm sample (m) Amount of blown SO.sub.2 gas 12,000 28,000 16,000 10,000 12,000 16,000 16,000 16,000 30,500 (cc/min) Treatment temperature 570 to 410 560 to 400 570 to 420 580 to 410 560 to 410 560 to 400 580 to 440 580 to 450 580 to 430 ( C.)

(28) In each of the glass sheets of Examples 1 to 6, the etching rate of the bottom surface was 10 nm/min or more, and the ratio (ER.sub.2/ER.sub.1) between the etching rate (ER.sub.1) of the bottom surface and the etching rate (ER.sub.2) of the top surface was 0.8 or less. As described above, the bottom surface is more susceptible to etching because a tin layer is formed in the bottom surface kept in contact with molten tin during formation into a sheet, and thus its etching rate tends to increase. On the other hand, the dealkalized glass surface is less susceptible to etching because a layer densified by dehydration condensation is formed therein, and thus its etching rate tends to decrease. Presumably, in the bottom surface of each of the glass sheets of Examples 1 to 6, an increase in the etching rate by the tin layer and a decrease in the etching rate by the densified dealkalized layer occurred simultaneously, resulting in an etching rate of 10 to 12 nm/min. In the top surface, only a phenomenon of a decrease in the etching rate by the densified dealkalized layer occurred, resulting in a lower etching rate of 6 to 8 nm/min. That is, in Examples 1 to 6, the degree of densification of the bottom surface by dealkalization was reduced to a relatively low level, and therefore the relation of ER.sub.2/ER.sub.10.8 was achieved. Thereby, in each of the glass sheets of Examples 1 to 6, a good balance was achieved between alkali ion exchange in the top surface and that in the bottom surface during chemical strengthening and thus warping was reduced.

(29) In each of the samples of Examples 3 to 6 having a ratio ER.sub.2/ER.sub.1 of 0.7 or less, the amount of warping was smaller than that of each of the samples of Examples 1 and 2 having a ratio ER.sub.2/ER.sub.1 of 0.8.

(30) On the other hand, in each of the glass sheets of Comparative Examples 1 to 3, the value of ER.sub.2/ER.sub.1 was more than 0.8. That is, in the glass sheets of Comparative Examples 1 to 3, the degree of densification of the bottom surface was higher than that in the glass sheets of Examples 1 to 6, and thus the etching rate of the bottom surface was lower. As a result, the degree of densification-derived inhibition of alkali ion exchange in the bottom surface increased during chemical strengthening, and alkali ion exchange in the top surface and that in the bottom surface were ill-balanced. This is presumably the reason why the amount of warping increased.

Example 7

(31) A glass sheet was produced in the same manner as in Examples 1 to 6 except that the thickness of the glass sheet was 0.4 mm, that SO.sub.2 gas was blown onto both the top surface and the bottom surface thereof, and that the treatment was performed with the amount of blown SO.sub.2 gas and at the treatment temperature as shown in Table 2. For the glass sheet obtained, the etching rate was measured, chemical strengthening was performed, and the amount of warping was measured in the same manner as in Examples 1 to 6. Table 2 shows the results.

Comparative Example 4

(32) A glass sheet was produced in the same manner as in Examples 1 to 6 except that the thickness of the glass sheet was 0.4 mm and that the treatment was performed with the amount of blown SO.sub.2 gas and at the treatment temperature as shown in Table 2. For the glass sheet obtained, the etching rate was measured, chemical strengthening was performed, and the amount of warping was measured in the same manner as in Examples 1 to 6. Table 2 shows the results.

(33) TABLE-US-00002 TABLE 2 Comparative Example 7 Example 4 Etching rate of bottom surface: ER.sub.1 (nm/min) 5.4 5.2 Etching rate of top surface: ER.sub.2 (nm/min) 3.8 5 ER.sub.2/ER.sub.1 0.7 1.0 Amount of warping of chemically strengthened 0.52 0.99 370 mm 470 mm sample (mm) Amount of warping of chemically strengthened 43.4 48.6 50 mm 50 mm sample (m) Amount of SO.sub.2 gas blown to bottom surface 30,000 30,000 (cc/min) Amount of SO.sub.2 gas blown to top surface 16,000 0 (cc/min) Treatment temperature ( C.) 560 to 420 560 to 420

Examples 8 to 11

(34) Glass sheets were produced in the same manner as in Examples 1 to 6 except that the thickness of the glass sheets was 0.7 mm and that the treatment was performed with the amounts of blown SO.sub.2 gas and at the treatment temperatures as shown in Table 3. For each of the glass sheets obtained, the etching rate was measured, chemical strengthening was performed, and the amount of warping was measured in the same manner as in Examples 1 to 6 except that the chemical strengthening was performed under the following conditions: the temperature of the molten salt of KNO.sub.3: 420 C.; and the immersion time: 4 hours. Only the samples having a size of 370 mm470 mm were subjected to the chemical strengthening and the measurement of the amount of warping. Table 3 shows the results.

Comparative Examples 5 and 6

(35) Glass sheets were produced in the same manner as in Examples 1 to 6 except that the thickness of the glass sheets was 0.7 mm and that the treatment was performed with the amounts of blown SO.sub.2 gas and at the treatment temperatures as shown in Table 3. For each of the glass sheets obtained, the etching rate was measured, chemical strengthening was performed, and the amount of warping was measured in the same manner as in Examples 1 to 6 except that the chemical strengthening was performed under the following conditions: the temperature of the molten salt of KNO.sub.3: 420 C.; and the immersion time: 4 hours. Only the samples having a size of 370 mm470 mm were subjected to the chemical strengthening and the measurement of the amount of warping. Table 3 shows the results.

(36) TABLE-US-00003 TABLE 3 Examples Comparative Examples Ex. 8 Ex. 9 Ex. 10 Ex. 11 Com. Ex. 5 Com. Ex. 6 Etching rate of bottom 9.7 13.5 15.4 10.3 6.6 7.1 surface: ER.sub.1 (nm/min) Etching rate of top 6.5 6.7 6.6 1.8 6.0 7.0 surface: ER.sub.2 (nm/min) ER.sub.2/ER.sub.1 0.7 0.5 0.4 0.2 0.9 1.0 Amount of warping of 0.45 0.37 0.31 0.23 1.29 1.06 chemically strengthened 370 mm 470 mm sample (mm) Amount of SO.sub.2 gas blown to 30,000 30,000 16,000 30,000 28,000 16,000 bottom surface (cc/min) Amount of SO.sub.2 gas blown to 0 0 0 20,000 0 0 top surface (cc/min) Treatment temperature ( C.) 540 to 410 510 to 390 510 to 390 540 to 420 540 to 380 540 to 380

(37) In the glass sheet samples having a thickness of 0.7 mm, the amount of warping after chemical strengthening in the samples of Examples 8 to 11 satisfying ER.sub.2/ER.sub.1 of 0.8 or less was smaller than that in the samples of Comparative Examples 5 and 6 having ER.sub.2/ER.sub.1 of more than 0.8.

(38) The results obtained in the above Examples 1 to 11 and Comparative Examples 1 to 6 revealed that in a glass sheet having ER.sub.2/ER.sub.1 of 0.8 or less, the difference between the amount of alkali ions exchanged in the top surface and that in the bottom surface by chemical strengthening was reduced and thereby warping of the glass sheet was reduced.

INDUSTRIAL APPLICABILITY

(39) The glass sheet of the present invention has a surface densified by dehydration condensation through dealkalization and further has reduced warping after chemical strengthening. Therefore, the glass sheet of the present invention is suitable for applications that require thinness and strength, for example, for use as a cover glass for protecting the surface of an image display of a mobile device.