Patent Application
20250059080
The present specification generally relates to glass compositions suitable for use as cover glass for electronic devices. More specifically, the present specification is directed to ion exchangeable glasses that may be formed into cover glass for electronic devices.
The mobile nature of portable devices, such as smart phones, tablets, portable media players, personal computers, and cameras, makes these devices particularly vulnerable to accidental dropping on hard surfaces, such as the ground. These devices typically incorporate cover glasses, which may become damaged upon impact with hard surfaces. In many of these devices, the cover glasses function as display covers, and may incorporate touch functionality, such that use of the devices is negatively impacted when the cover glasses are damaged.
There are two major failure modes of cover glass when the associated portable device is dropped on a hard surface. One of the modes is flexure failure, which is caused by bending of the glass when the device is subjected to dynamic load from impact with the hard surface. The other mode is sharp contact failure, which is caused by introduction of damage to the glass surface. Impact of the glass with rough hard surfaces, such as asphalt, granite, etc., can result in sharp indentations in the glass surface. These indentations become failure sites in the glass surface from which cracks may develop and propagate.
Glass can be made more resistant to flexure failure by the ion-exchange technique, which involves inducing compressive stress in the glass surface. However, the ion-exchanged glass will still be vulnerable to dynamic sharp contact, owing to the high stress concentration caused by local indentations in the glass from the sharp contact.
It has been a continuous effort for glass makers and handheld device manufacturers to improve the resistance of handheld devices to sharp contact failure. Solutions range from coatings on the cover glass to bezels that prevent the cover glass from impacting the hard surface directly when the device drops on the hard surface. However, due to the constraints of aesthetic and functional requirements, it is very difficult to completely prevent the cover glass from impacting the hard surface.
It is also desirable that portable devices be as thin as possible. Accordingly, in addition to strength, it is also desired that glasses to be used as cover glass in portable devices be made as thin as possible. Thus, in addition to increasing the strength of the cover glass, it is also desirable for the glass to have mechanical characteristics that allow it to be formed by processes that are capable of making thin glass-based articles, such as thin glass sheets or substrates.
Accordingly, a need exists for glasses that can be strengthened, such as by ion exchange, and that have the mechanical properties that allow them to be formed as thin glass-based articles.
According to aspect (1), a glass comprises:
According to aspect (2), aspect (1) comprises greater than or equal to 0.2 mol % to less than or equal to 1.0 mol % ZrO2.
According to aspect (3), any of aspects (1) through (2) comprise greater than or equal to 0.3 mol % to less than or equal to 0.9 mol % ZrO2.
According to aspect (4), any of aspects (1) through (3) comprise greater than or equal to 51.0 mol % to less than or equal to 60.0 mol % SiO2.
According to aspect (5), any of aspects (1) through (4) comprise greater than or equal to 16.5 mol % to less than or equal to 19.5 mol % Al2O3.
According to aspect (6), any of aspects (1) through (5) comprise greater than or equal to 3.5 mol % to less than or equal to 9.0 mol % B2O3.
According to aspect (7), any of aspects (1) through (6) comprise greater than or equal to 2.0 mol % to less than or equal to 10.0 mol % MgO.
According to aspect (8), any of aspects (1) through (7) comprise greater than or equal to 2.0 mol % to less than or equal to 7.0 mol % MgO.
According to aspect (9), any of aspects (1) through (8) comprise greater than or equal to 1.0 mol % to less than or equal to 6.5 mol % CaO.
According to aspect (10), any of aspects (1) through (9) comprise greater than 0 mol % to less than or equal to 3.5 mol % ZnO.
According to aspect (11), any of aspects (1) through (10) comprise greater than 0 mol % to less than or equal to 2.1 mol % ZnO.
According to aspect (12), any of aspects (1) through (11) comprise greater than or equal to 8.9 mol % to less than or equal to 12.0 mol % Li2O.
According to aspect (13), any of aspects (1) through (12) comprise greater than 1.8 mol % to less than or equal to 4.3 mol % Na2O.
According to aspect (14), any of aspects (1) through (13) comprise greater than 0 mol % to less than or equal to 1.0 mol % K2O.
According to aspect (15), any of aspects (1) through (14) comprise greater than or equal to 0.1 mol % to less than or equal to 1.0 mol % K2O.
According to aspect (16), any of aspects (1) through (15) comprise greater than 0 mol % to less than or equal to 2.5 mol % Y2O3.
According to aspect (17) any of aspects (1) through (16) comprise greater than 0 mol % to less than or equal to 1.5 mol % Y2O3.
According to aspect (18) any of aspects (1) through (17) comprise greater than 0 mol % to less than or equal to 0.3 mol % SnO2.
According to aspect (19) any of aspects (1) through (18) comprise greater than 0 mol % to less than or equal to 0.3 mol % TiO2.
According to aspect (20), any of aspects (1) through (19), wherein (Li2O+Na2O+MgO+CaO)/(Al2O3+ZrO2) is from 0.98 to 1.07.
According to aspect (21), any of aspects (1) through (20), wherein (Li2O+Na2O+MgO+CaO)/(Al2O3+ZrO2) is from 0.98 to 1.04.
According to aspect (22), any of aspects (1) through (21) comprise:
According to aspect (23), any of aspects (1) through (22) comprise:
According to aspect (24), any of aspects (1) through (23) comprise a fracture toughness K1C greater than or equal to 0.7.
According to aspect (25), any of aspects (1) through (24) comprise a fracture toughness K1C greater than or equal to 0.75.
According to aspect (26), any of aspects (1) through (24) comprise a fracture toughness K1C greater than or equal to 0.7 and less than or equal to 0.9.
According to aspect (27), any of aspects (1) through (26) comprise a 107.6 P softening point less than or equal to 850° C.
According to aspect (28), any of aspects (1) through (27) comprise a 107.6 P softening point greater than or equal to 750° C. less than or equal to 850° C.
According to aspect (29), any of aspects (1) through (30) comprise a 107.6 P softening point greater than or equal to 750° C. less than or equal to 835° C.
According to aspect (30), any of aspects (1) through (24) comprise a liquidus viscosity of greater than or equal to 200 poise to less than or equal to 4000 poise.
According to aspect (31), an article comprises:
According to aspect (32), an article comprises:
According to aspect (33), the glass-based substrate of any of aspects (31) through (32) comprise greater than 0.2 mol % to less than or equal to 1.0 mol % ZrO2.
According to aspect (34), the glass-based substrate of any of aspects (31) through (33) comprise greater than 0.3 mol % to less than or equal to 0.9 mol % ZrO2.
According to aspect (35), the glass-based substrate of any of aspects (31) through (34) comprise greater than or equal to 51.0 mol % to less than or equal to 60.0 mol % SiO2.
According to aspect (36), the glass-based substrate of any of aspects (31) through (35) comprise greater than or equal to 16.5 mol % to less than or equal to 19.5 mol % Al2O3.
According to aspect (37), the glass-based substrate of any of aspects (31) through (36) comprise greater than or equal to 3.5 mol % to less than or equal to 9.0 mol % B2O3.
According to aspect (38), the glass-based substrate of any of aspects (31) through (37) comprise greater than or equal to 2.0 mol % to less than or equal to 10.0 mol % MgO.
According to aspect (39), the glass-based substrate of any of aspects (31) through (38) comprise greater than or equal to 2.0 mol % to less than or equal to 7.0 mol % MgO.
According to aspect (40), the glass-based substrate of any of aspects (31) through (39) comprise greater than or equal to 1.0 mol % to less than or equal to 6.5 mol % CaO.
According to aspect (41), the glass-based substrate of any of aspects (31) through (40) comprise greater than or equal to 0 mol % to less than or equal to 2.1 mol % ZnO.
According to aspect (42), the glass-based substrate of any of aspects (31) through (41) comprise greater than or equal to 8.9 mol % to less than or equal to 12.0 mol % Li2O.
According to aspect (43), the glass-based substrate of any of aspects (31) through (42) comprise greater than 1.8 mol % to less than or equal to 4.3 mol % Na2O.
According to aspect (44), the glass-based substrate of any of aspects (31) through (43) comprise greater than or equal to 0.1 mol % to less than or equal to 1.0 mol % K2O.
According to aspect (45), the glass-based substrate of any of aspects (31) through (44) comprise greater than or equal to 0 mol % to less than or equal to 1.5 mol % Y2O3.
According to aspect (46), a the glass-based substrate of any of aspects (31) through (45), wherein (Li2O+Na2O+MgO+CaO)/(Al2O3+ZrO2) is from 0.98 to 1.07.
According to aspect (47), the glass-based substrate of any of aspects (31) through (46), wherein (Li2O+Na2O+MgO+CaO)/(Al2O3+ZrO2) is from 0.98 to 1.04.
According to aspect (48), the glass-based substrate of any of aspects (31) through (47) comprise:
According to aspect (49), the glass-based substrate of any of aspects (31) through (48) comprise:
According to aspect (50), the glass-based substrate of any of aspects (31) through (49) comprise a fracture toughness K1C greater than or equal to 0.7.
According to aspect (51), the glass-based substrate of any of aspects (31) through (50) comprise a fracture toughness K1C greater than or equal to 0.75.
According to aspect (52), the glass-based substrate of any of aspects (31) through (51) comprise a fracture toughness K1C greater than or equal to 0.7 and less than or equal to 0.9.
According to aspect (53), the glass-based substrate of any of aspects (31) through (52) comprise a 107.6 P softening point less than or equal to 850° C.
According to aspect (54), the glass-based substrate of any of aspects (31) through (53) comprise a 107.6 P softening point greater than or equal to 750° C. less than or equal to 850° C.
According to aspect (55), the glass-based substrate of any of aspects (31) through (54) comprise a 107.6 P softening point greater than or equal to 750° C. less than or equal to 835° C.
According to aspect (56), the glass-based substrate of any of aspects (31) through (55) comprise a liquidus viscosity of greater than or equal to 200 poise to less than or equal to 4000 poise.
According to aspect (57), the glass-based substrate of any of aspects (31) through (56) comprises a CS greater than or equal to 1 GPa.
According to aspect (58), the glass-based substrate of any of aspects (31) through (57) comprises a CT greater than or equal to 195 MPa.
According to aspect (59), the article of any of aspects (31) through (58) is a consumer electronic device, comprising:
According to aspect (60), the article of any of aspects (31) through (59) is the glass-based substrate.
According to aspect (61), the glass-based substrate of any of aspects (31) through (60) is transparent.
According to aspect (62), the glass-based substrate of any of aspects (31) through (61) has a thickness greater than or equal to 0.2 mm to less than or equal to 2.0 mm.
According to aspect (63), a method comprises:
According to aspect (64), the molten salt bath of aspect (63) comprises NaNO3.
According to aspect (65), the molten salt bath of any of aspects (63) through (64) comprises KNO3.
According to aspect (66), the molten salt bath of any of aspects (63) though (65) is at a temperature greater than or equal to 400° C. to less than or equal to 550° C.
According to aspect (67), the ion exchanging of any of aspects (63) through (66) extends for a time period greater than or equal to 0.5 hours to less than or equal to 48 hours.
According to aspect (68), the method of any of aspects (63) through (67) further comprises ion exchanging the glass-based substrate in a second molten salt bath.
According to aspect (69), the second molten salt bath of aspect (68) comprises KNO3.
Reference will now be made in detail to lithium aluminosilicate glasses according to various embodiments. Lithium aluminosilicate glasses have good ion exchangeability, and chemical strengthening processes have been used to achieve high strength and high toughness properties in lithium aluminosilicate glasses. Lithium aluminosilicate glasses are highly ion exchangeable glasses with high glass quality. The substitution of Al2O3 into the silicate glass network increases the interdiffusivity of monovalent cations during ion exchange. By chemical strengthening in a molten salt bath (e.g., KNO3 or NaNO3), glasses with high strength, high toughness, and high indentation cracking resistance can be achieved. The stress profiles achieved through chemical strengthening may have a variety of shapes that increase the drop performance, strength, toughness, and other attributes of the glass-based substrates.
Therefore, lithium aluminosilicate glasses with good physical properties, chemical durability, and ion exchangeability have drawn attention for use as cover glass. In particular, lithium containing aluminosilicate glasses, which have higher fracture toughness and reasonable raw material costs, are provided herein. Through different ion exchange processes, greater central tension (CT), depth of compression (DOC), and high compressive stress (CS) can be achieved. However, the addition of lithium in the aluminosilicate glass may reduce the melting point, softening point, or liquidus viscosity of the glass.
Specifically, lithium aluminosilicate glasses containing 0.1 mol % to 1.5 mol % ZrO2 are provided. The use of ZrO2 in a composition space where ZrO2 had not been previously introduced leads to an unexpectedly good combination of properties including high fracture toughness, high overall compressive stress (measured by CT), high surface compressive stress (CS), low softening point and low liquidus, making the glass compositions disclosed herein leading candidates for next-gen cover glass and also readily useable with certain convenient manufacturing processes such as slot-draw and fusion.
In embodiments of glass compositions described herein, the concentration of constituent components (e.g., SiO2, Al2O3, Li2O, and the like) are given in mole percent (mol %) on an oxide basis, unless otherwise specified. Components of the alkali aluminosilicate glass composition according to embodiments are discussed individually below. It should be understood that any of the variously recited ranges of one component may be individually combined with any of the variously recited ranges for any other component. As used herein, a trailing 0 in a number is intended to represent a significant digit for that number. For example, the number “1.0” includes two significant digits, and the number “1.00” includes three significant digits.
As utilized herein, a “glass-based” substrate refers to substrate that is made of glass or glass-ceramic. A “glass-based substrate” includes substrates that have been ion-exchanged, as well as substrates that have not been ion-exchanged. An “article” may be made wholly or partly of glass-based materials, such as glass substrates that include a surface coating, or electronic devices that include a glass substrate.
Drop performance is a leading attribute for glass-based substrates incorporated into mobile electronic devices. Fracture toughness and stress at depth are critical for improved drop performance on rough surfaces. For this reason, maximizing the amount of stress that can be provided in a glass before reaching frangibility limit increases the stress at depth and the rough surface drop performance. The fracture toughness is known to control the frangibility limit and increasing the fracture toughness increases the frangibility limit. The glass compositions disclosed herein have a high fracture toughness and are capable of achieving high compressive stress levels while remaining non-frangible. These characteristics of the glass compositions enable the development of improved stress profiles designed to address particular failure modes. This capability allows the ion exchanged glass-based substrates produced from the glass compositions described herein to be customized with different stress profiles to address particular failure modes of concern.
In the glass compositions described herein, SiO2 is the largest constituent and, as such, SiO2 is the primary constituent of the glass network formed from the glass composition. Pure SiO2 has a relatively low coefficient of thermal expansion (CTE). However, pure SiO2 has a high melting point. Accordingly, if the concentration of SiO2 in the glass composition is too high, the formability of the glass composition may be diminished as higher concentrations of SiO2 increase the difficulty of melting the glass, which, in turn, adversely impacts the formability of the glass. If the concentration of SiO2 in the glass composition is too low the chemical durability of the glass may be diminished, and the glass may be susceptible to surface damage during post-forming treatments. In embodiments, the glass composition generally comprises SiO2 in an amount of greater than or equal to 50.4 mol % to less than or equal to 60.5 mol % SiO2, such as greater than or equal to 51.0 mol % to less than or equal to 60.0 mol % SiO2, greater than or equal to 52.0 mol % to less than or equal to 55.0 mol % SiO2; and all ranges and sub-ranges between the foregoing values.
The glass compositions include Al2O3. Al2O3 may serve as a glass network former, similar to SiO2. Al2O3 may increase the viscosity of the glass composition due to its tetrahedral coordination in a glass melt formed from a glass composition, decreasing the formability of the glass composition when the amount of Al2O3 is too high. However, when the concentration of Al2O3 is balanced against the concentration of SiO2 and the concentration of alkali oxides in the glass composition, Al2O3 can reduce the liquidus temperature of the glass melt, thereby enhancing the liquidus viscosity and improving the compatibility of the glass composition with certain forming processes. The inclusion of Al2O3 in the glass compositions contributes to the high fracture toughness values described herein. In embodiments, the glass composition comprises Al2O3 in a concentration of from greater than or equal to 16.0 mol % to less than or equal to 20.0 mol %, such as greater than or equal to 16.5 mol % to less than or equal to 19.5 mol %, greater than or equal to 16.6 mol % to less than or equal to 19.5 mol %, greater than or equal to 18.5 mol % to less than or equal to 19.5 mol %, and all ranges and sub-ranges between the foregoing values.
The glass compositions described herein include B2O3. The inclusion of B2O3 increases the fracture toughness of the glass. In particular, the glass compositions include boron in the trigonal configuration, which increases the Knoop scratch threshold and fracture toughness of the glasses. If too much B2O3 is included in the composition, the amount of compressive stress imparted in an ion exchange process may be reduced and volatility at free surfaces during manufacturing may increase to undesirable levels. In embodiments, the glass composition comprises B2O3 in an amount from greater than or equal to 2.4 mol % to less than or equal to 9.5 mol %, such as greater than or equal to 3.5 mol % to less than or equal to 9.0 mol %, greater than or equal to 3.8 mol % to less than or equal to 8.5 mol %, greater than or equal to 5.0 mol % to less than or equal to 7.0 mol %, and all ranges and sub-ranges between the foregoing values.
The glass compositions described herein may include MgO. MgO may lower the viscosity of a glass, which enhances the formability and manufacturability of the glass. The inclusion of MgO in a glass composition may also improve the strain point and the Young's modulus of the glass composition. However, if too much MgO is added to the glass composition, the liquidus viscosity may be too low for compatibility with desirable forming techniques. The addition of too much MgO may also increase the density and the CTE of the glass composition to undesirable levels. The inclusion of MgO in the glass composition also helps to achieve the high fracture toughness values described herein. In embodiments, the glass composition comprises MgO in an amount from greater than or equal to 0 mol % to less than or equal to 11.0 mol %, such as greater than 2.0 mol % to less than or equal to 10.0 mol %, greater than 3.0 mol % to less than or equal to 10.0 mol %, greater than or equal to 2.0 mol % to less than or equal to 7.0 mol %, greater than or equal to 3.0 mol % to less than or equal to 5.0 mol %, and all ranges and sub-ranges between the foregoing values. In embodiments, the glass composition is substantially free or free of MgO. As used herein, the term “substantially free” means that the component is not purposefully added as a component of the batch material even though the component may be present in the final glass composition in very small amounts as a contaminant, such as less than 0.1 mol %.
The glass compositions described herein may include CaO. CaO may lower the viscosity of a glass, which may enhance the formability, the strain point, and the Young's modulus. However, if too much CaO is added to the glass composition, the density and the CTE of the glass composition may increase to undesirable levels and the ion exchangeability of the glass may be undesirably impeded. The inclusion of CaO in the glass composition also helps to achieve the high fracture toughness values described herein. In embodiments, the glass composition comprises CaO in an amount from greater than or equal to 0.4 mol % to less than or equal to 7.5 mol %, such as greater than or equal to 1.0 mol % to less than or equal to 6.5 mol %, greater than or equal to 1.0 mol % to less than or equal to 6.1 mol %, greater than or equal to 1.5 mol % to less than or equal to 2.5 mol %, and all ranges and sub-ranges between the foregoing values. In embodiments, the glass composition is substantially free or free of CaO.
The glass compositions described herein may include ZnO. ZnO may lower the viscosity of a glass, which may enhance the formability, the strain point, and the Young's modulus. However, if too much ZnO is added to the glass composition, the density and the CTE of the glass composition may increase to undesirable levels. The inclusion of ZnO in the glass composition also helps to achieve the high fracture toughness values described herein and provides protection against UV induced discoloration. In embodiments, the glass composition comprises ZnO in an amount from greater than or equal to 0 mol % to less than or equal to 3.5 mol %, such as greater than 0 mol % to less than or equal to 2.1 mol %, greater than or equal to 0 mol % to less than or equal to 0.5 mol %, greater than or equal to 0.2 mol % to less than or equal to 0.8 mol %, greater than or equal to 0.3 mol % to less than or equal to 0.7 mol %, greater than or equal to 0.4 mol % to less than or equal to 0.6 mol %, greater than or equal to 0.1 mol % to less than or equal to 0.5 mol %, greater than or equal to 0 mol % to less than or equal to 0.3 mol %, and all ranges and sub-ranges between the foregoing values. In embodiments, the glass composition is substantially free or free of ZnO.
The glass compositions described herein include Li2O. The inclusion of Li2O in the glass composition allows for better control of an ion exchange process and further reduces the softening point of the glass, thereby increasing the manufacturability of the glass. The presence of Li2O in the glass compositions can also allow the formation of a stress profile with a parabolic shape. The Li2O in the glass compositions help achieve the high fracture toughness values described herein. In embodiments, the glass composition comprises Li2O in an amount from greater than or equal to 7.4 mol % to less than or equal to 13.0 mol %, such as greater than or equal to 8.9 mol % to less than or equal to 12.0 mol %, greater than or equal to 9.0 mol % to less than or equal to 10.0 mol %, greater than or equal to 11.0 mol % to less than or equal to 12.5 mol %, and all ranges and sub-ranges between the foregoing values.
The glass compositions described herein include Na2O. Na2O may aid in the ion-exchangeability of the glass composition, and improve the formability, and thereby manufacturability, of the glass composition. However, if too much Na2O is added to the glass composition, the CTE may be too low, and the melting point may be too high. Additionally, if too much Na2O is included in the glass relative to the amount of Li2O the ability of the glass to achieve a deep depth of compression when ion exchanged may be reduced. In embodiments, the glass composition comprises Na2O in an amount from greater than or equal to 0.4 mol % to less than or equal to 5.5 mol %, such as greater than or equal to 1.8 mol % to less than or equal to 4.3 mol %, greater than or equal to 1.0 mol % to less than or equal to 3.0 mol %, and all ranges and sub-ranges between the foregoing values.
The glass compositions described herein may include K2O. The inclusion of K2O in the glass composition increases the potassium diffusivity in the glass, enabling a deeper depth of a compressive stress spike (DOLSP) to be achieved in a shorter amount of ion exchange time. If too much K2O is included in the composition the amount of compressive stress imparted during an ion-exchange process may be reduced. In embodiments, the glass composition comprises K2O in an amount from greater than or equal to 0 mol % to less than or equal to 1.0 mol %, such as greater than or equal to 0.1 mol % to less than or equal to 1.0 mol %, greater than or equal to 0.3 mol % to less than or equal to 0.8 mol %, greater than or equal to 0.4 mol % to less than or equal to 0.6 mol %, and all ranges and sub-ranges between the foregoing values. In embodiments, the glass composition is substantially free or free of K2O.
The glass compositions described herein include ZrO2. The inclusion of ZrO2 in the glass composition increases a fracture toughness of the glass composition. However, ZrO2 generally can have a low solubility in glass compositions, which can lead to undesirable zircon formation during manufacture. Methods can be used to reduce zircon formation such as avoiding the use of certain manufacturing equipment, such as zircon isopipes, that can encourage secondary zircon formation. The compositions and methods disclosed herein may allow for higher solubility of ZrO2 in the glass compositions compared to traditional glass compositions and methods of forming. In embodiments, the glass composition comprises ZrO2 in an amount from greater than or equal to 0.1 mol % to less than or equal to 1.5 mol %, such as greater than or equal to 0.2 mol % to less than or equal to 1.1 mol %, greater than or equal to 0.2 mol % to less than or equal to 1.0 mol %, greater than or equal to 0.3 mol % to less than or equal to 0.9 mol %, greater than or equal to 0.4 mol % to less than or equal to 0.8 mol %, greater than or equal to 0.5 mol % to less than or equal to 0.8 mol %, greater than or equal to 0.6 mol % to less than or equal to 0.8 mol %, and all ranges and sub-ranges between the foregoing values.
The glass compositions may include Y2O3. The inclusion of Y2O3 in the glass increases the solubility of ZrO2, which can decrease secondary zircon formation. ZrO2 has limited solubility and is particularly desirable for the compositions disclosed herein, so increasing the solubility is desirable. However, Y2O3 is expensive relative to other materials of the glass compositions. In embodiments, the glass composition comprises Y2O3 in an amount from greater than or equal to 0 mol % to less than or equal to 2.5 mol %, such as greater than or equal to 0 mol % to less than or equal to 1.5 mol %, greater than or equal to 0 mol % to less than or equal to 1.0 mol %, greater than or equal to 0 mol % to less than or equal to 0.5 mol %, greater than or equal to 0.1 mol % to less than or equal to 1.5 mol %, greater than or equal to 0.1 mol % to less than or equal to 1.0 mol %, greater than or equal to 0.1 mol % to less than or equal to 0.5 mol %, and all ranges and sub-ranges between the foregoing values. In embodiments, the glass composition is substantially free or free of Y2O3.
The glass compositions may include TiO2. The inclusion of TiO2 in the glass increases UV absorption. In embodiments, the glass composition comprises TiO2 in an amount from greater than or equal to 0 mol % to less than or equal to 0.5 mol %, such as greater than or equal to 0 mol % to less than or equal to 0.3 mol %, greater than or equal to 0 mol % to less than or equal to 0.2 mol %, greater than or equal to 0 mol % to less than or equal to 0.1 mol %, greater than or equal to 0.05 mol % to less than or equal to 0.3 mol %, greater than or equal to 0.05 mol % to less than or equal to 0.2 mol %, greater than or equal to 0.05 mol % to less than or equal to 0.15 mol %, greater than or equal to 0.05 mol % to less than or equal to 0.2 mol %, and all ranges and sub-ranges between the foregoing values. In embodiments, the glass composition is substantially free or free of TiO2.
The glass compositions may optionally include one or more fining agents. In embodiments, the fining agent may include, for example, SnO2. In embodiments, SnO2 may be present in the glass composition in an amount less than or equal to 0.3 mol %, such as from greater than or equal to 0 mol % to less than or equal to 0.3 mol %, greater than or equal to 0 mol % to less than or equal to 0.2 mol %, greater than or equal to 0 mol % to less than or equal to 0.1 mol %, greater than or equal to 0 mol % to less than or equal to 0.05 mol %, greater than or equal to 0.1 mol % to less than or equal to 0.3 mol %, greater than or equal to 0.1 mol % to less than or equal to 0.2 mol %, and all ranges and sub-ranges between the foregoing values. In some embodiments, the glass composition may be substantially free or free of SnO2. In embodiments, the glass composition may be substantially free of one or both of arsenic and antimony. In other embodiments, the glass composition may be free of one or both of arsenic and antimony.
The glass compositions described herein may be formed primarily from SiO2, Al2O3, B2O3, CaO, Li2O, Na2O, ZrO2, and optionally MgO, ZnO and K2O. In embodiments, the glass compositions are substantially free or free of components other than SiO2, Al2O3, B2O3, CaO, Li2O, Na2O, ZrO2, and optionally MgO, ZnO, K2O, Y2O3, and SnO2, in the amounts specified herein. In embodiments, the glass compositions are substantially free or free of components other than SiO2, Al2O3, B2O3, CaO, Li2O, Na2O, ZrO2, and a fining agent.
In embodiments, the glass composition may be substantially free or free of Fe2O3. Iron is often present in raw materials utilized to form glass compositions, and as a result may be detectable in the glass compositions described herein even when not actively added to the glass batch.
In embodiments, the glass composition may be substantially free or free of at least one of Ta2O5, HfO2, La2O3, and Y2O3. In embodiments, the glass composition may be substantially free or free of Ta2O5, HfO2, and La2O3. While these components may increase the fracture toughness of the glass when included, there are cost and supply constraints that make using these components undesirable for commercial purposes. Stated differently, the ability of the glass compositions described herein to achieve high fracture toughness values without the inclusion of Ta2O5, HfO2, and La2O3 provides a cost and manufacturability advantage.
The glass compositions described herein can have a (Li2O+Na2O+MgO+CaO)/(Al2O3+ZrO2) from 0.98 to 1.2, such as from 0.98 to 1.09, from 0.98 to 1.08, from 0.98 to 1.07, from 0.98 to 1.06, from 0.98 to 1.05, from 0.98 to 1.04, from 0.98 to 1.03, from 0.98 to 1.02, from 0.98 to 1.01, from 0.99 to 1.2, from 0.99 to 1.09, from 0.99 to 1.08, from 0.99 to 1.07, from 0.99 to 1.06, from 0.99 to 1.05, from 0.99 to 1.04, from 0.99 to 1.03, from 0.99 to 1.02, from 0.99 to 1.01, from 1.0 to 1.2, such as from 1.0 to 1.09, from 1.0 to 1.08, from 1.0 to 1.07, from 1.0 to 1.06, from 1.0 to 1.05, from 1.0 to 1.04, from 1.0 to 1.03, from 1.0 to 1.02, from 1.0 to 1.01, and all ranges and sub-ranges between the foregoing values. Without intending to be bound by any particular theory, it is believed that a (Li2O+Na2O+MgO+CaO)/(Al2O3+ZrO2) less than the values disclosed herein can decrease the solubility of ZrO2, which limits the amount of ZrO2 which can be incorporated in the glass composition. A glass composition with poor ZrO2 solubility may result in a poor liquidus viscosity. Further, it is believed a (Li2O+Na2O+MgO+CaO)/(Al2O3+ZrO2) greater than the values disclosed herein can results in poor scratch behavior.
Compressive stress layers may be formed in the glass by exposing the glass to an ion exchange medium. In embodiments, the ion exchange medium may be molten nitrate salt. In embodiments, the ion exchange medium may be a molten salt bath, and may include KNO3, NaNO3, or combinations thereof. In embodiments, other sodium and potassium salts may be used in the ion exchange medium, such as, for example sodium or potassium nitrites, phosphates, or sulfates. In embodiments, the ion exchange medium may include lithium salts, such as LiNO3. The ion exchange medium may additionally include additives commonly included when ion exchanging glass, such as silicic acid. The ion exchange process is applied to a glass-based substrate to form a glass-based substrate that includes a compressive stress layer extending from a surface of the glass-based substrate to a depth of compression and a central tension region. The glass-based substrate utilized in the ion exchange process may include any of the glass compositions described herein.
In embodiments, the ion exchange medium comprises NaNO3. The sodium in the ion exchange medium exchanges with lithium ions in the glass to produce a compressive stress. In embodiments, the ion exchange medium may include NaNO3 in an amount of less than or equal to 95 wt %, such as less than or equal to 90 wt %, less than or equal to 80 wt %, less than or equal to 70 wt %, less than or equal to 60 wt %, less than or equal to 50 wt %, less than or equal to 40 wt %, less than or equal to 30 wt %, less than or equal to 20 wt %, less than or equal to 10 wt %, or less. In embodiments, the ion exchange medium may include NaNO3 in an amount of greater than or equal to 5 wt %, such as greater than or equal to 10 wt %, greater than or equal to 20 wt %, greater than or equal to 30 wt %, greater than or equal to 40 wt %, greater than or equal to 50 wt %, greater than or equal to 60 wt %, greater than or equal to 70 wt %, greater than or equal to 80 wt %, greater than or equal to 90 wt %, or more. In embodiments, the ion exchange medium may include NaNO3 in an amount of greater than or equal to 0 wt % to less than or equal to 100 wt %, such as greater than or equal to 10 wt % to less than or equal to 90 wt %, greater than or equal to 20 wt % to less than or equal to 80 wt %, greater than or equal to 30 wt % to less than or equal to 70 wt %, greater than or equal to 40 wt % to less than or equal to 60 wt %, greater than or equal to 50 wt % to less than or equal to 90 wt %, and all ranges and sub-ranges between the foregoing values. In embodiments, the molten ion exchange medium includes 100 wt % NaNO3.
In embodiments, the ion exchange medium comprises KNO3. In embodiments, the ion exchange medium may include KNO3 in an amount of less than or equal to 95 wt %, such as less than or equal to 90 wt %, less than or equal to 80 wt %, less than or equal to 70 wt %, less than or equal to 60 wt %, less than or equal to 50 wt %, less than or equal to 40 wt %, less than or equal to 30 wt %, less than or equal to 20 wt %, less than or equal to 10 wt %, or less. In embodiments, the ion exchange medium may include KNO3 in an amount of greater than or equal to 5 wt %, such as greater than or equal to 10 wt %, greater than or equal to 20 wt %, greater than or equal to 30 wt %, greater than or equal to 40 wt %, greater than or equal to 50 wt %, greater than or equal to 60 wt %, greater than or equal to 70 wt %, greater than or equal to 80 wt %, greater than or equal to 90 wt %, or more. In embodiments, the ion exchange medium may include KNO3 in an amount of greater than or equal to 0 wt % to less than or equal to 100 wt %, such as greater than or equal to 10 wt % to less than or equal to 90 wt %, greater than or equal to 20 wt % to less than or equal to 80 wt %, greater than or equal to 30 wt % to less than or equal to 70 wt %, greater than or equal to 40 wt % to less than or equal to 60 wt %, greater than or equal to 50 wt % to less than or equal to 90 wt %, and all ranges and sub-ranges between the foregoing values. In embodiments, the molten ion exchange medium includes 100 wt % KNO3.
The ion exchange medium may include a mixture of sodium and potassium. In embodiments, the ion exchange medium is a mixture of potassium and sodium, such as a molten salt bath that includes both NaNO3 and KNO3. In embodiments, the ion exchange medium may include any combination NaNO3 and KNO3 in the amounts described above, such as a molten salt bath containing 80 wt % NaNO3 and 20 wt % KNO3.
The glass composition may be exposed to the ion exchange medium by dipping a glass substrate made from the glass composition into a bath of the ion exchange medium, spraying the ion exchange medium onto a glass substrate made from the glass composition, or otherwise physically applying the ion exchange medium to a glass substrate made from the glass composition to form the ion exchanged glass-based substrate. Upon exposure to the glass composition, the ion exchange medium may, according to embodiments, be at a temperature from greater than or equal to 360° C. to less than or equal to 500° C., such as greater than or equal to 370° C. to less than or equal to 490° C., greater than or equal to 380° C. to less than or equal to 480° C., greater than or equal to 390° C. to less than or equal to 470° C., greater than or equal to 400° C. to less than or equal to 460° C., greater than or equal to 410° C. to less than or equal to 450° C., greater than or equal to 420° C. to less than or equal to 440° C., greater than or equal to 430° C. to less than or equal to 470° C., greater than or equal to 400° C. to less than or equal to 470° C., greater than or equal to 380° C. to less than or equal to 470° C., and all ranges and sub-ranges between the foregoing values. In embodiments, the glass composition may be exposed to the ion exchange medium for a duration from greater than or equal to 10 minutes to less than or equal to 48 hours, such as greater than or equal to 10 minutes to less than or equal to 24 hours, greater than or equal to 0.5 hours to less than or equal to 24 hours, greater than or equal to 1 hours to less than or equal to 18 hours, greater than or equal to 2 hours to less than or equal to 12 hours, greater than or equal to 4 hours to less than or equal to 8 hours, and all ranges and sub-ranges between the foregoing values.
The ion exchange process may include a second ion exchange treatment. In embodiments, the second ion exchange treatment may include ion exchanging the glass-based substrate in a second molten salt bath. The second ion exchange treatment may utilize any of the ion exchange mediums described herein. In embodiments, the second ion exchange treatment utilizes a second molten salt bath that includes KNO3.
The ion exchange process may be performed in an ion exchange medium under processing conditions that provide an improved compressive stress profile as disclosed, for example, in U.S. Patent Application Publication No. 2016/0102011, which is incorporated herein by reference in its entirety. In some embodiments, the ion exchange process may be selected to form a parabolic stress profile in the glass-based substrates, such as those stress profiles described in U.S. Patent Application Publication No. 2016/0102014, which is incorporated herein by reference in its entirety.
After an ion exchange process is performed, it should be understood that a composition at the surface of an ion exchanged glass-based substrate is different than the composition of the pre-IOX glass substrate (i.e., the glass substrate before it undergoes an ion exchange process). This results from one type of alkali metal ion in the as-formed glass substrate, such as, for example Li+ or Na+, being replaced with larger alkali metal ions, such as, for example Na+ or K+, respectively. However, the glass composition at or near the center of the depth of the ion exchanged glass-based substrate will, in embodiments, still have the composition of the as-formed non-ion exchanged glass substrate. As utilized herein, the center of the glass-based substrate refers to any location in the glass-based substrate that is a distance of at least 0.5 t from every surface thereof, where t is the thickness of the glass-based substrate.
The glass-based substrates disclosed herein may be incorporated into an article such as an article with a display (or display articles) (e.g., consumer electronics, including mobile phones, tablets, computers, navigation systems, and the like), architectural articles, transportation articles (e.g., automobiles, trains, aircraft, sea craft, etc.), appliance articles, or any article that requires some transparency, scratch-resistance, abrasion resistance or a combination thereof. An exemplary article incorporating any of the glass-based articles disclosed herein is shown in
Physical properties of the glass compositions as disclosed above will now be discussed.
Glass compositions according to embodiments have a high fracture toughness. Without wishing to be bound by any particular theory, the high fracture toughness may impart improved drop performance to the glass compositions. The high fracture toughness of the glass compositions described herein increases the resistance of the glasses to damage and allows a higher degree of stress to be imparted to the glass through ion exchange, as characterized by central tension, without becoming frangible. As utilized herein, the fracture toughness refers to the KIC value as measured by the Double Cantilever Beam method unless otherwise noted. The Double Cantilever Beam (DCB) method utilized to measure the KIC value is disclosed in U.S. Pat. No. 11,634,354, the contents of which are incorporated herein by reference in its entirety. Additionally, the KIC values are measured on non-strengthened glass samples, such as measuring the KIC value prior to ion exchanging a glass-based substrate. The KIC values discussed herein are reported in MPa√m, unless otherwise noted.
In embodiments, the glass compositions exhibit a KIC value of greater than or equal to 0.7 MPa√m, such as greater than or equal to 0.75 MPa√m. In embodiments, the glass compositions exhibit a KIC value of greater than or equal to 0.7 MPa√m and less than or equal to 0.9. In embodiments, the glass compositions exhibit a KIC value of greater than or equal to 0.77 MPa√m, or greater than or equal to 0.8 MPa√m. In embodiments, the glass compositions exhibit a KIC value within any ranges and sub-ranges between the foregoing values.
The glass compositions described herein have liquidus viscosities that are compatible with manufacturing processes that are suitable for forming thin glass sheets. For example, the glass compositions are compatible with down draw processes such as fusion draw processes or slot draw processes. Embodiments of the glass-based substrates may be described as fusion-formable (i.e., formable using a fusion draw process). The fusion draw process uses a drawing tank that has a channel for accepting molten glass raw material. The channel may have weirs that are open at the top along the length of the channel on both sides of the channel. When the channel fills with molten material, the molten glass overflows the weirs. Due to gravity, the molten glass flows down the outside surfaces of the drawing tank as two flowing glass films. These outside surfaces of the drawing tank can extend down and inwardly so that they join at an edge below the drawing tank. The two flowing glass films can join at this edge to fuse and form a single flowing glass-based substrate. The fusion of the glass films produces a fusion line within the glass-based substrate, and this fusion line allows glass-based substrates that were fusion formed to be identified without additional knowledge of the manufacturing history. The fusion draw method offers the advantage that, because the two glass films flowing over the channel fuse together, neither of the outside surfaces of the resulting glass-based substrate comes in contact with any part of the apparatus. Thus, the surface properties of the fusion drawn glass-based substrate are not affected by such contact.
The glass compositions described herein may be selected to have liquidus viscosities that are compatible with fusion draw processes. Thus, the glass compositions described herein are compatible with existing forming methods, increasing the manufacturability of glass-based substrates formed from the glass compositions. As used herein, the term “liquidus viscosity” refers to the viscosity of a molten glass at the liquidus temperature, wherein the liquidus temperature refers to the temperature at which crystals first appear as a molten glass cools down from the melting temperature, or the temperature at which the very last crystals melt away as temperature is increased from room temperature. As used herein, the term “liquidus viscosity (internal)” refers to the liquidus viscosity in the internal bulk melted glass. As used herein, the term “liquidus viscosity (air)” refers to the liquidus viscosity of the melted glass composition at the air interface. As used herein, the term “liquidus viscosity (Platinum)” refers to the liquidus viscosity of the melted glass composition at the platinum boat interface. As used herein “liquidus viscosity” refers to the “liquidus viscosity (internal)”, unless stated otherwise. Unless specified otherwise, a liquidus viscosity value disclosed in this application is determined by the following method: First, the liquidus temperature of the glass is measured in accordance with ASTM C829-81 (2015), titled “Standard Practice for Measurement of Liquidus Temperature of Glass by the Gradient Furnace Method.” Next, the viscosity of the glass at the determined liquidus temperature is measured in accordance with ASTM C965-96 (2012), titled “Standard Practice for Measuring Viscosity of Glass Above the Softening Point”. The term “Vogel-Fulcher-Tamman (‘VFT’) relation,” as used herein, describes the temperature dependence of the viscosity and is represented by the following equation:
where η is viscosity. To determine VFT A, VFT B, and VFT T0, the viscosity of the glass composition is measured over a given temperature range. The raw data of viscosity versus temperature is then fit with the VFT equation by least-squares fitting to obtain A, B, and T0. With these values, a viscosity point (e.g., 200 P Temperature, 35000 P Temperature, and 200000 P Temperature) at any temperature above softening point may be calculated. Unless otherwise specified, the liquidus viscosity and temperature of a glass composition or substrate is measured before the composition or substrate is subjected to any ion-exchange process or any other strengthening process. In particular, the liquidus viscosity and temperature of a glass composition or substrate is measured before the composition or substrate is exposed to an ion-exchange solution, for example before being immersed in an ion-exchange solution. Where an ion exchanged substrate is described as having a liquidus viscosity, the reference is to the liquidus viscosity of the substrate prior to ion exchange. The pre-ion exchange composition may be determined by looking at the composition at the center of the substrate.
In embodiments the liquidus viscosity of the glass composition may be from 200 poise (P) to 4000 P, such as from 200 P to 3000 P, from 200 P to 2500 P, from 200 P to 2000 P, from 200 P to 1500 P, from 200 P to 1000 P, and all ranges and sub-ranges between the foregoing values.
In embodiments, the liquidus viscosity of the glass composition may be greater than or equal to 200 P. In embodiments, the liquidus viscosity of the glass composition may be less than or equal 4000 P, such as less than or equal to 3000 P, less than or equal to 2500 P, less than or equal to 2000 P, less than or equal to 1500 P, or less than or equal to 1000 P. A lower liquidus viscosity has been associated with higher KIC values and improved ion exchange capability, but when the liquidus viscosity is too low the manufacturability of the glass compositions is reduced.
In one or more embodiments, the glass compositions described herein may form glass-based substrates that exhibit an amorphous microstructure and may be substantially free of crystals or crystallites. In other words, the glass-based substrates formed from the glass compositions described herein may exclude glass-ceramic materials.
In embodiments, the glass compositions described herein can be strengthened, such as by ion exchange, making a glass-based substrate that is damage resistant for applications such as, but not limited to, display covers. With reference to
According to the convention normally used in the art, compression or compressive stress is expressed as a negative (<0) stress and tension or tensile stress is expressed as a positive (>0) stress. Throughout this disclosure, however, CS is expressed as a positive or absolute value—i.e., as recited herein, CS=|CS|. The compressive stress (CS) has a maximum at or near the surface of the glass-based substrate, and the CS varies with distance d from the surface according to a function. Referring again to
In embodiments, the CS of the glass-based substrates is from greater than or equal to 1000 MPa to less than or equal to 1500 MPa, such as greater than or equal to 1100 MPa to less than or equal to 1400 MPa, greater than or equal to 1200 MPa to less than or equal to 1300 MPa, and all ranges and sub-ranges between the foregoing values.
In embodiments, Na+ and K+ ions are exchanged into the glass-based substrate and the Na+ ions diffuse to a deeper depth into the glass-based substrate than the K+ ions. The depth of penetration of K+ ions (“Potassium DOL”, or “DOL”) is distinguished from DOC because it represents the depth of potassium penetration as a result of an ion exchange process. The Potassium DOL is typically less than the DOC for the substrates described herein. Potassium DOL is measured using a surface stress meter such as the commercially available FSM-6000 surface stress meter, manufactured by Orihara Industrial Co., Ltd. (Japan), which relies on accurate measurement of the stress optical coefficient (SOC), as described above with reference to the CS measurement. The potassium DOL may define a depth of a compressive stress spike (DOLSP), where a stress profile transitions from a steep spike region to a less-steep deep region. The deep region extends from the bottom of the spike to the depth of compression. The DOLSP of the glass-based substrates may be from greater than or equal to 3 μm to less than or equal to 10 μm, such as greater than or equal to 4 μm to less than or equal to 9 μm, greater than or equal to 5 μm to less than or equal to 8 μm, greater than or equal to 6 μm to less than or equal to 7 μm, and all ranges and sub-ranges between the foregoing values.
The compressive stress of both major surfaces (110, 112 in
The measurement of a maximum CT value is an indicator of the total amount of stress stored in the strengthened substrates, due to the force balancing described above. For this reason, the ability to achieve higher CT values correlates to the ability to achieve higher degrees of strengthening and increased performance. In embodiments, the glass-based substrates may have a maximum CT greater than or equal to 60 MPa, such as greater than or equal to 70 MPa, greater than or equal to 80 MPa, greater than or equal to 90 MPa, greater than or equal to 100 MPa, greater than or equal to 110 MPa, greater than or equal to 120 MPa, greater than or equal to 130 MPa, greater than or equal to 140 MPa, greater than or equal to 150 MPa, or more. In embodiments, the glass-based substrate may have a maximum CT of from greater than or equal to 60 MPa to less than or equal to 160 MPa, such as greater than or equal to 70 MPa to less than or equal to 160 MPa, greater than or equal to 80 MPa to less than or equal to 160 MPa, greater than or equal to 90 MPa to less than or equal to 160 MPa, greater than or equal to 100 MPa to less than or equal to 150 MPa, greater than or equal to 110 MPa to less than or equal to 140 MPa, greater than or equal to 120 MPa to less than or equal to 130 MPa, and all ranges and sub-ranges between the foregoing values.
The high fracture toughness values of the glass compositions described herein also may enable improved performance. The frangibility limit of the glass-based substrates produced utilizing the glass compositions described herein is dependent at least in part on the fracture toughness. For this reason, the high fracture toughness of the glass compositions described herein allows for a large amount of stored strain energy to be imparted to the glass-based substrates formed therefrom without becoming frangible. The increased amount of stored strain energy that may then be included in the glass-based substrates allows the glass-based substrates to exhibit increased fracture resistance, which may be observed through the drop performance of the glass-based substrates. The relationship between the frangibility limit and the fracture toughness is described in U.S. Patent Application Pub. No. 2020/0079689 A1, titled “Glass-based Articles with Improved Fracture Resistance,” published Mar. 12, 2020, the entirety of which is incorporated herein by reference. The relationship between the fracture toughness and drop performance is described in U.S. Patent Application Pub. No. 2019/0369672 A1, titled “Glass with Improved Drop Performance,” published Dec. 5, 2019, the entirety of which is incorporated herein by reference.
As noted above, DOC is measured using a scattered light polariscope (SCALP) technique known in the art. The DOC is provided in some embodiments herein as a portion of the thickness (t) of the glass-based substrate. In embodiments, the glass-based substrates may have a depth of compression (DOC) from greater than or equal to 0.20 t to less than or equal to 0.25 t, such as from greater than or equal to 0.21 t to less than or equal to 0.24 t, or from greater than or equal to 0.22 t to less than or equal to 0.23 t, and all ranges and sub-ranges between the foregoing values. The high DOC values produced when the glass compositions described herein are ion exchanged provide improved resistance to fracture, especially for situations where deep flaws may be introduced. For example, the deep DOC provides improved resistance to fracture when dropped on rough surfaces.
The ion-exchange conditions disclosed herein were not optimized for the glass compositions disclosed herein. As such, the data demonstrates that IOX is effective for these compositions and provides some examples of parameters that can be achieved. However, it is expected based on the disclosure herein that better parameters may be achieved, such as higher CT and CS.
Thickness (t) of glass-based substrate 100 is measured between surface 110 and surface 112. In embodiments, the thickness of glass-based substrate 100 may be in a range from greater than or equal to 0.1 mm to less than or equal to 4 mm, such as greater than or equal to 0.2 mm to less than or equal to 3.5 mm, greater than or equal to 0.3 mm to less than or equal to 3 mm, greater than or equal to 0.4 mm to less than or equal to 2.5 mm, greater than or equal to 0.5 mm to less than or equal to 2 mm, greater than or equal to 0.6 mm to less than or equal to 1.5 mm, greater than or equal to 0.7 mm to less than or equal to 1 mm, greater than or equal to 0.2 mm to less than or equal to 2 mm, and all ranges and sub-ranges between the foregoing values. The glass substrate utilized to form the glass-based substrate may have the same thickness as the thickness desired for the glass-based substrate.
Embodiments will be further clarified by the following examples. It should be understood that these examples are not limiting to the embodiments described above.
Glass compositions were prepared and analyzed. The analyzed glass compositions for Samples 1 through 45 and Comparative Example (C1) included the components listed in Tables 1-8 below and were prepared by conventional glass forming methods. In Tables 1-8, all components are in mol %, and the KIC fracture toughness was measured primarily with the Double Cantilever Beam (DCB) method described herein. The Poisson's ratio (v), the Young's modulus (E), and the shear modulus (G) of the glass compositions were measured by a resonant ultrasonic spectroscopy technique of the general type set forth in ASTM E2001-13, titled “Standard Guide for Resonant Ultrasound Spectroscopy for Defect Detection in Both Metallic and Non-metallic Parts.”. The refractive index at 589.3 nm and stress optical coefficient (SOC) of the substrates are also reported in Tables 1-8. The density of the glass compositions was determined using the buoyancy method of ASTM C693-93(2013).
The term “annealing point,” as used herein, refers to the temperature at which the viscosity of the glass composition is 1×1013,18 poise. The term “strain point,” as used herein, refers to the temperature at which the viscosity of the glass composition is 1×1014,68 poise. The strain point and annealing point of the glass compositions was determined using the fiber elongation method of ASTM C336-71(2015)
The term “softening point,” as used herein, refers to the temperature at which the viscosity of the glass composition is 1×107−6 poise. The softening point of the glass compositions was determined using the fiber elongation method of ASTM C336-71(2015).
The linear coefficient of thermal expansion (CTE) over the temperature range 0-300° C. is expressed in terms of ppm/° C. and was determined using a push-rod dilatometer in accordance with ASTM E228-11. The high-temperature coefficient of thermal expansion (High-T CTE) is expresses in in terms of ppm/° C. The phrase “high temperature coefficient of thermal expansion” or “High-T CTE,” as used herein, refers to the coefficient of thermal expansion of the glass above the glass transition temperature of the glass composition. The High-T CTE is determined by plotting the instantaneous CTE (y-axis) as a function of the temperature (x-axis). The High-T CTE is the value of the High-T CTE where the slope of the CTE v. temperature curve is approximately zero following a pronounced increase (i.e., where the CTE v. temperature curve “plateaus”). The value of the High-T CTE is a measure of the volume change of the glass during cooling and is an indication of the dimensional stability of the glass composition when the glass is utilized in conjunction with elevated temperature 3-D forming process including, without limitation, vacuum sagging forming processes.
Both before and after ion exchange, every sample was visually observed to have a transparency suitable for the cover glass of an electronic display, such as the electronic display of a cell phone.
Substrates with a thickness of0.5 mm were formed from the compositions of Tables 1-8, and subsequently ion exchanged to form example ion exchanges substrates. The ion exchange included submerging the substrates into a molten salt bath. The salt bath included 90 wt % K and 10 wt % NaNO3, and was at a temperature of 450° C. In Tables 9-12, the length of the ion exchange process, surface compressive stress (CS), the depth of layer (DOL), and the maximum central tension (CT) of the ion exchanged substrates are reported. The CS, DOL, and CT were measured according to the methods described herein.
This application claims the benefit of priority under 35 U.S.C. § 119 of U.S. Provisional Application Ser. No. 63/532,698 filed on Aug. 15, 2023, the content of which is relied upon and incorporated herein by reference in its entirety.
| Number | Date | Country | |
|---|---|---|---|
| 63532698 | Aug 2023 | US |
