CHEMICALLY TOUGHENABLE BORON-FREE FLOAT GLASS COMPOSITIONS

Abstract: A glass composition capable of being chemically strengthened by ion-exchange within 100 hours to provide a glass with a surface compressive stress of greater then 400MPa and an ion-exchange depth greater then 200 microns comprising: SiO2 58 % to 70 % (by weight), Al2O3 5 % to 15 %, Na2O 12 % to 18 %, K2O 0.1 % to 5 %, MgO 4 % to 10 %, CaO 0 % to 1 % with the provisos that the total of the Al2O3 and MgO is in excess of 13 %, the total of the amounts of Al2O3 plus MgO divided by the amount of K2O is at least 3 and that the sum of the amounts of Na2O, K2O and MgO is at least 22 %.

Description: CHEMICALLY TOUGHENABLE BORON-FREE FLOAT GLASS COMPOSITIONS The present invention relates to glasses which are capable of being chemically toughened. In particular the present invention relates to glasses which can be chemically toughened and which are primarily, but not essentially, intended for use in aeronautical and automotive vehicles. In the chemical toughening of glass, the surface of the glass is compressed by the substitution of alkali ions in the surface layers of the glass by heavier, larger ions. This is customarily effected in an ion-exchange bath containing one or more salts of the heavier ions. By so doing, the breaking strength of the glass is increased, thereby permitting the glass to withstand static stresses, such as those experienced in aircraft cockpits or cabins, and more dynamic stresses, such as those encountered if the aircraft strikes a flock of birds. Chemically strengthenable glasses are well known. Many of these contain significant quantities of lithium. In, for example, United States Patent Specification No. 4156755, there is described and claimed such a glass. However, lithium has the disadvantage of increasing the density of the glass and, in many modern applications for chemically toughened glass, this is not acceptable. An alternative method of chemically toughening glass if the glass contains sodium ions is to ion-exchange these for potassium ions. Such a method is disclosed in, for example, International (PCT) Patent Application No. WO 94/08910. Such glass has the added advantage that it has a low density of approximately 2.46 in comparison with conventional float glass which has a density of approximately 2.50. Although such patent alleges that no boron need be present in the glass, it is clear that the glass would be more difficult to melt if boron was absent. In fact, this is borne out by the sole example in the patent which discloses a composition containing nearly 3.5% B 2 O 3 . Boron oxide lowers the viscosity of the glass. This makes the glass easier to melt and, in theory, easier to refine. Moreover, the combination of, in the context of these glasses, high amounts of both boron and potassium allows the low density to be achieved. However, the use of boron is disadvantageous in that it attacks the silica crowns conventionally used in furnaces. The use of high quantities of potassium also has drawbacks. In particular, large amounts of potassium cause the production of high viscosity foams early in the melting process. These are very slow to collapse and often lead to silica faults in the finished glass which makes it unacceptable from a commercial viewpoint. It is desirable if the glasses produced have relatively high strain points so that the ion- exchange can be effected at higher temperatures and the desired level of chemical toughening can be achieved in an economically acceptable time. It is known that the strain point can be raised by increasing the quantities of alumina or zirconia in the glasses. However, these materials are extremely refractory and are difficult to melt in a conventional float furnace within an acceptable time. Alkali metal oxides, such as those of lithium, sodium and potassium help to digest alumina and zirconia but have an adverse effect on the strain point and prevent a high surface compressive stress being achieved during the ion- exchange. Alkaline earth metal oxides have also been utilised in making glasses which are chemically toughened by ion-exchange. However, these also have drawbacks associated therewith. Zinc oxide is not compatible with the float process, due to the ease with which it is reduced to zinc metal, thereby producing an unacceptable bloom on the glass. Calcium oxide interferes with the sodium/potassium ion-exchange and leads to poor penetration whilst magnesium oxide, particularly in the presence of alumina, normally raises the liquidus temperature of the glass to an unacceptably high level. It will be understood that glasses being manufactured on a float plant should have a positive working range, that is to say, a positive difference between the temperature at which the glass has a viscosity of 10,000 poise and the liquidus, also known as the crystallisation, temperature. The present invention therefore seeks to provide boron-free glasses having a positive working range, which can be readily melted to float glass standards with respect to the inclusion of bubble and solids and which can be chemically strengthened over a period of less than 100 hours to exhibit a surface stress of at least 400 MPa with a depth of ion penetration greater than 200 microns. In a subsidiary aspect, the present invention also seeks to provide a glass having a low density. In particular, a low density, in the context of the present invention, is less than 2.48 g/cm 3 , preferably less than 2.46 g/cm 3 . This is particularly true if the glass is intended for use in aeronautical applications. According to the present invention, there is therefore provided a boron-free float glass composition having a positive working range comprising:- SiO 2 58% to 70% (by weight) Al 2 O 3 5% to 15% Na 2 O 12% to 18% K 2 O 0.1% to 5% MgO 4% to 10% CaO 0% to 1% with the provisos that the sum of the Al 2 O 3 and MgO exceeds 13%, that the sum of the amounts of Al 2 O 3 plus MgO divided by the amount of K 2 O exceeds 3 and that the sum of the Na 2 O plus K 2 O plus MgO exceeds 22%. We have surprisingly found that the amount of Al 2 O 3 is critical. If the amount of Al 2 O 3 is less than 5%, insufficient stress can be created when the glass is toughened by ion- exchange but if it is greater than 15%, the glass becomes extremely difficult to melt and causes liquidus problems. MgO has been found to be a highly desirable component of the glasses of the present invention. It assists in lowering the melting temperature whilst simultaneously not affecting the strain point of the glass. Furthermore, it helps to increase the surface stress of the glass during the ion-exchange process. Both MgO and Al 2 O 3 help to achieve the high surface compressive stress required if the glass is to be used in aeronautical applications. However, when both are present in comparatively high amounts, as in the glasses of the present invention, they can have an adverse effect on the liquidus temperature of the glass. K 2 O poses many problems when melting glass in a float tank. For example, during the melting process, it causes foaming which breaks up into a scum and eventually appears in the finished glass as an inclusion fault. Nevertheless, in the context of the present invention, it is essential to assist in the diffusion of additional potassium ions from the ion-exchange bath so as to achieve sufficiently deep penetration at a reasonable rate. We have surprisingly found that if the amounts of Al 2 O , MgO and K 2 O are as outlined above, the above-mentioned problems do not arise or are at least minimised. CaO is often used to lower the melting point of glasses. However, its presence in glasses of the present invention lead to low ion penetration during the ion exchange. It is, therefore, not specifically included in the glasses of the present invention but some CaO may be present as an impurity such as, for example, if the glasses of the present invention are being made in a non-dedicated furnace and CaO was present in the composition previously made in that furnace. In preferred embodiments of the present invention, other constituents may be present in the composition. For example, iron oxide, which gives glasses containing it a green coloration can be used. If used, the iron will be present in both its ferrous and ferric forms. Ferric iron absorbs radiation in the ultraviolet portion of the electromagnetic spectrum whilst ferrous iron absorbs in the infra-red portion. If iron is to be used, the amount thereof and the ratio of ferrous to ferric iron will be selected in dependence, usually, upon the intended use of the glass. Since iron reduces the visible light transmission of the glass, this is clearly undesirable in aeronautical applications and in communication and detection systems which operate using infra-red beams. In such circumstances, therefore, the amount of iron present is maintained low, that is to say, below 0.2% , preferably below 0.05%. Similarly, the amount of ferrous iron present is maintained as low as possible, that is to say, below 20% and ideally below 15%. On the other hand, if the glass is intended for use in surface vehicles, the absorption of infra-red radiation and ultraviolet radiation are desirable. In such a case, therefore, the amount of iron present may be as much as 2% or higher and the ferrous level may be as high as 40%. To remove the green coloration, other additives such as cobalt, selenium and/or nickel may be included in the composition. If it is desired to improve the ultraviolet absorption of the glass, additives such as cerium or titanium may be included in the composition. Float glasses are conventionally refined using sulphate, generally identified as SO 3 , and carbon. However, the usual amounts of these materials added to the composition of the present invention causes excessive foaming . We have found that the glass may be readily refined if the amount of SO 3 present in the batch is limited to 0.1% to 0.4%. The potassium salt used for the ion-exchange may be any suitable salt such as the sulphate, the chloride or mixtures thereof. However, for their general ease of use and for their melting range the nitrates are preferred. The ion-exchange medium may be formed into a paste with an inert medium such as oxides of iron, titanium or silicon as is well known in the art. As is also known per se. the ion-exchange may be accelerated, if desired, by the application of an electric field to the process. Polished samples of the glasses were strengthened by ion-exchange in a chemical bath containing 99.5% KNO and 0.5% silicic acid at temperatures ranging from 400°C to 460°C for periods of from 25 hours to 240 hours. Temperatures of below 400°C may be used but, if a large ion-exchange bath is being employed, there is the possibility of the temperature in localised regions dropping below the melting point of the potassium nitrate. Similarly, temperatures of over 500°C may be employed but, at this temperature level, the potassium nitrate begins to decompose which can have deleterious effects on the quality of the glass and may also release noxious fumes. Following immersion, the glasses were allowed to drain for 30 minutes and were then cooled in air to ambient temperature. Residual salt was washed from the glass and the surface stress and the depth of the compressive layer were measured using a Differential Stress Refractometer. The data was modified to take into account changes in the refractive index of the composition and of the stress optical coefficient. Birefringence was related to applied stress, the comparison being made with a conventional soda-lime-silica glass as made by the float process. The data obtained were combined to predict how long the ion-exchange treatment would need to be continued at a selected temperature to achieve a pre-determined surface stress and compressive depth. Compositions having the desired predicted properties were then prepared as samples for strength testing, were treated for the predicted length of time and were then strength tested to destruction. The invention will be further described, by way of example, with reference to the following non-limitative Examples:- TABLE t% Glass Si0 2 B 2 0 3 A1 2 0 3 Na 2 0 K 2 0 MgO CaO TiOj Zr0 2 P.03 Ce0 2 F^Oj S0 3 No. 1 62.30 0.00 8.80 15.80 4.90 7.80 0.20 0.00 0.00 0.00 0.00 0.02 0.20 2 64.70 0.00 6.50 15.00 4.50 8.90 0.20 0.00 0.00 0.00 0.00 0.02 0.20 3 65.80 0.00 5.50 14.10 4.50 9.50 0.20 0.00 0.00 0.00 0.20 0.02 0.22 4 66.20 0.00 6.50 14.70 4.30 7.90 0.20 0.00 0.00 0.00 0.00 0.02 0.20 5 63.40 0.00 8.80 15.30 3.90 8.20 0.20 0.00 0.00 0.00 0.00 0.02 0.20 6 64.49 0.00 9.20 15.30 3.90 6.30 0.50 0.00 0.00 0.00 0.00 0.02 0.31 7 61.50 0.00 13.10 15.00 3.90 5.90 0.50 0.00 0.00 0.00 0.00 0.02 0.10 8 64.60 0.00 10.00 15.20 3.90 5.30 0.90 0.00 0.00 0.00 0.00 0.02 0.10 9 63.60 0.00 11.00 15.80 3.60 5.20 0.50 0.00 0.00 0.00 0.00 0.02 0.31 10 64.50 0.00 10.10 15.60 3.60 6.00 0.00 0.00 0.00 0.00 0.00 0.02 0.20 11 61.70 0.00 14.10 16.00 3.50 4.50 0.00 0.00 0.00 0.00 0.00 0.02 0.20 σ> 12 65.50 0.00 8.80 15.30 3.20 6.80 0.20 0.00 0.00 0.00 0.00 0.02 0.19 13 63.40 0.00 8.80 16.00 3.20 8.20 0.20 0.00 0.00 0.00 0.00 0.02 0.20 14 65.00 0.00 10.10 16.00 2.50 6.20 0.00 0.00 0.00 0.00 0.00 0.02 0.17 15 65.00 0.00 10.30 16.40 2.00 6.10 0.00 0.00 0.00 0.00 0.00 0.02 0.16 16 64.80 0.00 11.00 17.60 0.60 5.80 0.00 0.00 0.00 0.00 0.00 0.02 0.20 17 65.80 0.00 10.60 17.40 0.00 5.60 0.40 0.00 0.00 0.00 0.00 0.02 0.17 18 63.10 0.00 10.90 15.60 3.60 5.10 0.50 0.00 0.00 0.00 0.00 1.00 0.20 19 62.40 0.00 10.80 15.50 3.50 5.10 0.50 0.00 0.00 0.00 0.00 2.00 0.20 20 61.20 0.00 10.60 15.20 3.50 5.00 0.50 0.00 0.00 0.00 0.00 3.80 0.20 21 63.10 0.00 10.90 15.60 3.60 5.10 0.50 1.00 0.00 0.00 0.00 0.02 0.20 22 63.10 0.00 10.90 15.60 3.60 5.10 0.50 0.00 1.00 0.00 0.00 0.02 0.20 -) 23 63.10 0.00 10.90 15.60 3.60 5.10 0.50 0.00 0.00 1.00 0.00 0.02 0.20 n H 24 54.00 0.00 17.50 20.20 0.60 7.50 0.00 0.00 0.00 0.00 0.00 0.02 0.20 5 25 68.50 0.00 6.30 14.70 3.60 6.50 0.20 0.00 0.00 0.00 0.00 0.02 03 0.20 26 71.10 0.00 3.00 14.20 3.60 7.70 0.20 0.00 0.00 0.00 0.00 0.02 0.20 © © 27 66.20 3.40 4.80 11.90 6.10 7.10 0.30 0.00 0.00 0.00 0.00 0.08 0.10 00 as 28 72.70 0.00 1.10 13.00 0.60 3.90 8.30 0.05 0.00 0.00 0.00 0.11 0.25 TABLE (continued) Time taken to achieve -400 MPa Temperature required to achieve surface stress and 200 microns 400 MPa surface stress and Surface stress (MPa) achieved O Glass No. Fe 2" (AljOyfMgO) (Al-Λ+MgOVKjO compressive 1 depth 200 miσons compresive depth at 430°C after 81 hours (hours) CO 00 1 18 16.6 3.4 66 to 71 437 to 438 420 2 19 15.4 3.4 101 to 102 434 444 3 10 15.0 3.3 16 to 31 471 515 4 19 14.4 3.3 72 to 74 438 to 439 439 5 19 17.0 4.4 19 to 31 462 to 470 512 6 16 15.5 4.0 42 to 61 445 to 455 434 7 19 19.0 4.9 1 1 to 13 504 to 507 670 8 20 15.3 3.9 48 to 57 439 to 443 409 9 17 16.2 4.5 48 to 58 437 to 441 407 10 18 16.1 4.5 35 to 39 446 to 448 441 11 18 18.6 5.3 2 to 12 493 to 464 477 12 17 15.6 4.9 35 to 37 455 to 456 454 13 18 17.0 5.3 84 to 94 443 to 444 505 14 19 16.3 6.5 97 to 105 423 to 425 396 15 18 16.4 8.2 32 to 61 442 to 459 435 16 19 16.8 28.0 81 to 108 427 to 433 414 17 - 16.2 - 114 to 121 424 to 426 408 18 36 16.0 4.4 16 to 19 473 to 477 474 19 23 15.9 4.5 20 to 21 475 563 20 22 15.6 4.5 39 to 48 457 to 459 577 21 18 16.0 4.4 41 to 64 440 to 453 426 22 17 16.0 4.4 17 to 22 465 to 470 513 23 - 16.0 4.4 45 to 52 438 to 441 383 24 - 25.0 41.7 10 to 11 500 to 510* 442 25 - 12.8 3.6 147 to 149 407 to 408 364 "0 26 - 10.7 3.0 898 to 1332 351 to 357 342 o H 27 - 11.9 2.0 84 to 88 450 to 451 496 O 28 - 5.0 8.3 3896 to 4337 400 to 401 462 CS o o Note * denotes temperature © restricted to 510°C as salt would © oo (3\ decompose at higher temperatures TABLE (continued) Property ≥ Temp, at Temp, at Thermal oo 00 Glass 10" poise IO 40 poise Annealing Strain point T (Liquidus) Density expansion A. No. (°C) (°C) point (°C) ro (°C) (8 cm 3 ) coefficient (100-300°C (xlO- 7 /°C) 1 1362 1067 - 920 2.480 - 2 1362 1068 - - 970 2.469 - 3 1364 1072 572 539 1056 2.468 103.8 4 1388 1081 - - 920 2.463 - 5 1382 1085 - - 1070 2.475 - 6 1431 1112 553 513 950 2.457 • 7 1478 1157 583 545 1006 2.463 100.5 8 1438 1112 549 511 912 2.458 102.5 9 1427 1103 560 524 939 2.560 106.0 10 1432 1110 571 534 - 2.456 - 11 . - 585 546 - 2.457 105.6 CO 12 1422 1098 567 531 925 2.455 100.5 13 1374 1078 - - 1043 2.472 - 14 1436 1114 579 541 - 2.455 - 15 1438 1106 579 544 903 2.454 - 16 1437 1119 - - - 2.453 99.5 17 1442 1125 587 553 - 2.454 . 18 1432 1116 563 526 - 2.469 - 19 1427 1111 - - 909 2.476 . 20 1413 1106 565 527 948 2.495 . 21 1422 1105 - - - 2.470 . 22 - - - - - 2.476 - 23 1439 1110 569 534 960 2.457 104.0 O H 24 1368 1092 613 577 1150 2.504 108.5 O 25 1418 1101 - - - 2.442 . CO 26 1393 1080 - - - 2.436 • © 27 1346 1043 548 513 - 2.456 98.5 © oo 28 1335 1035 554 523 1000 2.502 89.5 In the Examples given above, Examples 1 to 16 inclusive show basic compositions in accordance with the present invention. In Examples 18 and 19, the effect of adding iron oxide (Fe 2 O 3 ) is shown. In Example 20, the iron content has been raised to 3.8% and it can be seen that the chemical strengthening properties have not been impaired but the density of the glass has increased. Examples 21 and 22 show that the addition of 1% by weight of, respectively TiO 2 .and ZrO 2 do not adversely affect the chemical strengthening properties but, like high quantities of iron, do increase the density of the glass. Example 23 includes phosphorus and although it can be seen that the chemical strengthening properties are not affected, phosphorus has high corrosive effects on the refractories of the furnace. Example 24 shows that a higher content of Na 2 O and Al 2 O 3 substantially increase the density of the glass and mean that it has a negative working range. This Example is, therefore, a comparative Example. Examples 17,25,26,27 and 28 are further comparative Examples. Example 25 shows that if the aluminium oxide plus magnesium oxide content is lower than 13%, the time required to strengthen the glass to a desired depth is substantially increased. Example 26 shows that the same problem is encountered if the aluminium oxide content is less than 5%. Example 17 shows that the presence of less than 0.1% potassium oxide permits the desired chemical strengthening to be achieved but, again, the time taken to achieve this is long. Example 27 is a commercial ion-exchange glass containing boron which, as aforementioned, is not used in the present invention due to the necessity of providing a dedicated furnace with boron resistant refractory materials. Finally, Example 28 is a standard window float glass.

Claims: 10 CLAIMS 1. A boron-free float glass composition capable of being chemically strengthened over a period of less than 100 hours to exhibit a surface stress of at least 400 MPa with a depth of ion penetration greater than 200 microns comprising:- SiO 2 58% to 70% (by weight) Al 2 O 3 5% to 15% Na 2 O 12% to 18% K 2 O 0.1% to 5% MgO 4% to 10% CaO 0% to 1% with the provisos that the sum of the Al 2 O 3 and MgO exceeds 13%, that the sum of the amounts of Al 2 O 3 plus MgO divided by the amount of K 2 O exceeds 3 and that the sum of the Na 2 O plus K 2 O plus MgO exceeds 22%. 2. A composition as claimed in Claim 1 additionally containing Fe 2 O 3 in an amount of from 0.2% to 4% by weight, the ferrous state being at least 20%. 3. A composition as claimed in Claim 1 additionally containing Fe 2 O in an amount of less than 0.2% by weight. 4. A composition as claimed in Claim 3 additionally including cerium oxide in an amount of from 0.05% to 0.5% by weight. 5. A composition as claimed in Claim 3 or 4 wherein the ferrous state is less than 20%. 6. A composition as claimed in any one of Claims 1 to 5 additionally containing TiO 2 in an amount of up to 1% by weight. 7. A composition as claimed in any preceding Claim additionally containing sulphate in an amount of from 0.1% to 0.4% by weight. 11 8. A composition as claimed in any one of Claims 2 to 7 additionally including a colorant for neutralising the green colour produced by the Fe 2 O 3 . 9. A composition as claimed in Claim 8 wherein the colorant is selected from cobalt oxide, nickel oxide or selenium or mixtures thereof. 10. A composition as claimed in any preceding claim in which the Al 2 O 3 is present in an amount in excess of 6% by weight and the MgO is present in an amount of from 4% to 8% by weight. 11. A composition as claimed in any one of Claims 1 to 9 in which the MgO is present in an amount in excess of 8% by weight and the Al 2 O 3 is present in an amount of from 5% to 9% by weight. 12. A composition as claimed in any preceding Claim in which the K 2 O is present in an amount of from 0.5% to 3.5% by weight and the Al 2 O 3 is present in an amount of from 5.5% to 11% by weight. 13. A composition as claimed in Claim 1 substantially as hereinbefore described with reference to the foregoing Examples.

Inventors: BRADSHAW JOHN MICHAEL, LYTHGOE STANLEY, SMITH IAN HEATON, TORR ASHLEY CARL, BRADSHAW, JOHN, MICHAEL, LYTHGOE, STANLEY, SMITH, IAN, HEATON, TORR, ASHLEY, CARL
Applicants: BRADSHAW JOHN MICHAEL, LYTHGOE STANLEY, PILKINGTON PLC, SMITH IAN HEATON, TORR ASHLEY CARL, BRADSHAW, JOHN, MICHAEL, LYTHGOE, STANLEY, SMITH, IAN, HEATON, TORR, ASHLEY, CARL
Application year: 1999
Main classification: C03C3
IPC codes: C03C3, C03C21