Patent Grant
12116311
This disclosure relates to glass-based articles exhibiting improved damage resistance, including improved fracture resistance, and more particularly to glass and glass ceramic articles exhibiting a non-zero metal oxide concentration gradient or concentration that varies along a substantial portion of the thickness.
Glass-based articles often experience severe impacts that can introduce large flaws into a surface of such articles. Such flaws can extend to depths of up to about 200 micrometers (microns, or m) from the surface. Traditionally, thermally tempered glass has been used to prevent failures caused by the introduction of such flaws into the glass because thermally tempered glass often exhibits large compressive stress (CS) layers (e.g., approximately 21% of the total thickness of the glass), which can prevent the flaws from propagating further into the glass and thus, can prevent failure. An example of a stress profile generated by thermal tempering is shown in
Thermal tempering is currently limited to thick glass-based articles (i.e., glass-based articles having a thickness t1 of about 3 millimeters or greater) because, to achieve the thermal strengthening and the desired residual stresses, a sufficient thermal gradient must be formed between the core of such articles and the surface. Such thick articles are undesirable or not practical in many applications such as display (e.g., consumer electronics, including mobile phones, tablets, computers, navigation systems, and the like), architecture (e.g., windows, shower panels, countertops etc.), transportation (e.g., automotive, trains, aircraft, sea craft, etc.), appliance, or any application that requires superior fracture resistance but thin and light-weight articles.
Although chemical strengthening is not limited by the thickness of the glass-based article in the same manner as thermally tempering, known chemically strengthened glass-based articles do not exhibit the stress profile of thermally tempered glass-based articles. An example of a stress profile generated by chemical strengthening (e.g., by an ion exchange process), is shown in
Accordingly, there is a need for thin glass-based articles that exhibit improved fracture resistance.
A first aspect of the present disclosure pertains to a glass-based article including a first surface and a second surface opposing the first surface defining a thickness (t); a concentration of a metal oxide that is both non-zero and varies along a thickness range from about 0·t to about 0.3·t; and a central tension (CT) region comprising a maximum CT greater than or equal to 71.5/√(t), wherein, when the glass-based article is fractured, the glass-based article fractures into at least 2 fragments/inch2 (fragments per square inch), wherein the sample size used was a 5.08 cm by 5.08 cm (2 inch by 2 inch) square, as measured by the “Frangibility Test”, as described Z. Tang, et al. Automated Apparatus for Measuring the Frangibility and Fragmentation of Strengthened Glass. Experimental Mechanics (2014) 54:903-912. The number of fragments is divided by the area of the sample being tested (in square inches). As used herein, the variation in metal oxide concentration may be referred to herein as a metal oxide concentration gradient. In one or more embodiments, the concentration of the metal oxide is non-zero and varies along the entire thickness. In one or more embodiments, the CT region may include the metal oxide that is both non-zero and that varies along a thickness range from about 0·t to about 0.3·t. The glass-based article of one or more embodiments may include a thickness t of about 3 millimeters (mm) or less, 2 mm or less, or about 1 mm or less.
A second aspect of this disclosure pertains to a glass-based article including a first surface and a second surface opposing the first surface defining a thickness (t) of about 3 millimeters or less, and a stress profile extending along the thickness, wherein all points of the stress profile between a thickness range from about 0·t up to 0.3·t and from greater than 0.7·t to t, comprise a tangent having a slope with an absolute value that is greater than about 0.1 MPa/micrometers, wherein the stress profile comprises a maximum CS, a DOC and a maximum CT greater than or equal to 71.5/√(t), wherein the ratio of maximum CT to absolute value of maximum CS is in the range from about 0.01 to about 0.2 and wherein the DOC is about 0.1·t or greater.
A third aspect of this disclosure pertains to a glass-based article including a first surface and a second surface opposing the first surface defining a thickness (t); and a concentration of a metal oxide that is both non-zero and varies along a thickness range from about 0·t to about 0.3·t (or from about 0·t to about 0.4·t or from about 0·t to about 0.45·t), a surface compressive stress of greater than about 200 MPa or greater; and a CT region having a maximum CT greater than or equal to 71.5/√(t).
A fourth aspect of this disclosure pertains to a glass-based article comprising: a first surface and a second surface opposing the first surface defining a thickness (t); and a metal oxide that forms a concentration gradient, wherein the concentration of the metal oxide decreases from the first surface to a value at a point between the first surface and the second surface and increases from the value to the second surface, wherein the concentration of the metal oxide at the point is non-zero, and wherein the glass-based article comprises a stored tensile energy of about greater than 0 J/m2 to less than 20 J/m2 and a Young's modulus of about 70 GPa or greater.
A fifth aspect of this disclosure pertains to a glass-based article comprising: a first surface and a second surface opposing the first surface defining a thickness (t) of about 3 millimeters or less; and a stress profile extending along the thickness, wherein the stress profile at all points between a thickness range from about 0t up to 0.3t and from greater than 0.7t, comprise a tangent having a slope with an absolute value of greater than about 0.1 MPa/micrometer, wherein the stress profile comprises a maximum CS, a DOC and a maximum CT, wherein the ratio of maximum CT to absolute value of maximum CS is in the range from about 0.01 to about 0.2 and wherein the DOC is about 0.1·t or greater, and wherein the glass-based article comprises a stored tensile energy of about greater than 0 J/m2 to less than 20 J/m2 and a Young's modulus of about 70 GPa or greater. In one or more embodiments, the glass-based article includes a non-zero concentration of a metal oxide that continuously varies along the entire thickness. In some instances, the non-zero concentration of a metal oxide that continuously varies along thickness segments of less than about 10 micrometers.
A sixth aspect of this disclosure pertains to a glass-based article including a stress profile including a CS region and a CT region, wherein the CT region is approximated by the equation Stress(x)=MaxT−(((CTn·(n+1))/0.5n)·|(x/t)−0.5|n), wherein MaxT is a maximum tension value, CTn is less than or equal to MaxT and is a positive value in units of MPa, x is position along the thickness (t) in micrometers, and n is between 1.5 and 5. In some embodiments, the maximum CT value in the range from about 50 MPa to about 250 MPa and the maximum CT value is at a depth in the range from about 0.4t to about 0.6t. In one or more embodiments, from a thickness in the range from about 0t to about 0.1t, the stress profile comprises a slope in the range from about 20 MPa/micrometer to about 200 MPa/micrometer. In one or more embodiments, the stress profile is approximated by a plurality of error functions as measured from 0.5t to the surface.
In accordance with one or more embodiments of the glass-based articles described herein, a monovalent ion of the metal oxide generates a stress along the thickness range (i.e., from about 0·t to about 0.3·t, from about 0·t to about 0.4·t, or from about 0·t to about 0.45·t).
The concentration of the metal oxide of one or more embodiments decreases from the first surface to a value at a point between the first surface and the second surface and increases from the value to the second surface.
In one or more embodiments, the concentration of the metal oxide is about 0.05 mol % or greater throughout the thickness. For example, in one or more embodiments, the concentration of the metal oxide at the first surface is about 1.5 times (or more) greater than the concentration of the metal oxides at a depth equal to about 0.5·t. In exemplary embodiments, the glass-based article comprises a total concentration of the metal oxide in the range from about 1 mol % to about 15 mol %. In one or more embodiments, examples of the metal oxide include any one or more of Li2O, Na2O, K2O, Rb2O, and Cs2O. In one or more embodiments, the monovalent ion of the metal oxide has a largest ionic diameter of all of the total metal oxides in the glass-based substrate or article.
In one or more embodiments, the CT region comprises the metal oxide that is both non-zero and that varies along a thickness range from about 0·t to about 0.3·t. In one or more embodiments of the glass-based articles described herein, the maximum CT is greater than or equal to 71.5/√(t) (MPa), wherein “71.5” is in units of MPa·(mm){circumflex over ( )}{circumflex over ( )}0.5, and “t” is in millimeters (mm).
The glass-based article of some embodiments includes a first metal oxide concentration and a second metal oxide concentration. In some embodiments, the first metal oxide concentration is in the range from about 0 mol % to about 15 mol % from a first thickness range from about 0·t to about 0.5·t. In some embodiments, the second metal oxide concentration is in the range from about 0 mol % to about 10 mol % from a second thickness range from about 0 micrometers to about 25 micrometers. The glass-based article may include an optional third metal oxide.
In one or more embodiments, the glass-based articles described herein may exhibit a surface compressive stress (CS) that is greater than the maximum CT. One or more embodiments of the glass-based articles described herein may include a surface CS of about 300 MPa or greater. In some instances, this surface CS is exhibited when the glass-based article has a thickness of about 2 mm or less. In one or more embodiments, the glass-based article exhibits a combination of a surface CS of about 200 MPa or greater and a chemical depth of layer of about 0.4·t or greater. In one or more embodiments, the glass-based article includes a CS extending from the first surface to a DOC, wherein the DOC is about 0.1·t or greater. In some instances, the ratio of maximum CT to absolute value of surface CS is in the range from about 0.1 to about 0.8.
In one or more embodiments, the glass-based article has an amorphous structure. In some embodiments, the glass-based article may include a crystalline structure.
In one or more embodiments, the glass-based articles described herein may exhibit a transmittance of about 88% or greater over a wavelength in the range from about 380 nm to about 780 nm. In some instances, the glass-based articles described herein may exhibit CIELAB color space coordinates, under a CIE illuminant F02, of L* values of about 88 and greater, a* values in the range from about −3 to about +3, and b* values in the range from about −6 to about +6.
In one or more embodiments, the glass-based articles described herein may include a Young's modulus of about 70 GPa or greater. In some embodiments, the glass-based articles described herein include a liquidus viscosity of less than about 100 kilopoise (kP). In one or more embodiments, the glass-based articles described herein exhibit a fracture toughness (K1C) of about 0.65 MPa·mm1/2 or greater. In one or more embodiments, the glass-based articles described herein include any one or more of: a composition comprising a combined amount of Al2O3 and Na2O of about 15 mol % or less, a composition comprising about 4 mol % or greater Na2O, a composition comprising any one or more of B2O3 and ZnO, and a composition substantially free of P2O5. In one or more embodiments, glass-based article comprises a monovalent ion (e.g., sodium ion or potassium ion) diffusivity of about 450 μm2/hour (square micrometers per hour) or greater at about 460° C. In some embodiments, this monovalent ion diffusivity is exhibited in combination with a DOC greater than about 0.15·t, and a surface CS that is 1.5 times the maximum CT or greater.
In one or more embodiments, the glass-based articles described herein exhibit certain fracture behavior. For example, in one or more embodiments, when the glass-based article is fractured by a single event (i.e., a single impact such as being dropped or being impacted once with an implement), the glass-based article fractures into at least 2 fragments/inch2-(fragments per square inch), wherein the sample size used was a 5.08 cm by 5.08 cm (2 inch by 2 inch) square, as measured by the “Frangibility Test”, as described Z. Tang, et al. Automated Apparatus for Measuring the Frangibility and Fragmentation of Strengthened Glass. Experimental Mechanics (2014) 54:903-912. The number of fragments is divided by the area of the sample being tested (in square inches). In some embodiments, when the glass-based article is fractured, the glass-based article fractures into at least 1 fragment/inch2 up to 40 fragments/inch2 (fragments per square inch), wherein the sample size used was a 5.08 cm by 5.08 cm (2 inch by 2 inch) square.
A seventh aspect of this disclosure pertains to a use of a glass substrate in a strengthened glass-based article. In one or more embodiments, the glass substrate comprises (in mol %): SiO2 in an amount in the range from about 68 to about 75; Al2O3 in an amount in the range from about 12 to about 15; B2O3 in an amount in the range from about 0.5 to about 5; Li2O in an amount in the range from about 2 to about 10; Na2O in an amount in the range from about 0 to about 6; MgO in an amount in the range from about 1 to about 4; ZnO in an amount in the range from about 0 to about 3; and CaO in an amount in the range from about 0 to about 5, wherein the glass substrate is ion-exchangeable and is amorphous. In one or embodiments, the glass substrate exhibits any one or more of: a ratio of Li2O to R2O in the range from about 0.45 to about 1; a difference between a total amount of R2O to the amount of Al2O3 in the range from about −5 to about 0; a difference between a total amount of RxO (in mol %) and the amount of Al2O3 in the range from about 0 to about 3; and a ratio of the amount of MgO (in mol %) to a total amount of RO (in mol %) in the range from about 0 to about 1, and wherein the glass substrate is substantially free of nucleating agents.
A eighth aspect of this disclosure pertains to a glass substrate comprising a composition including, in mol %, SiO2 in an amount in the range from about 68 to about 75; Al2O3 in an amount in the range from about 12 to about 15; B2O3 in an amount in the range from about 0.5 to about 5; Li2O in an amount in the range from about 2 to about 10; Na2O in an amount in the range from about 0 to about 6; MgO in an amount in the range from about 1 to about 4; ZnO in an amount in the range from about 0 to about 3; and CaO in an amount in the range from about 0 to about 5, wherein the glass substrate is ion-exchangeable and is amorphous. In one or more embodiments, the glass substrate exhibits any one or more of: a ratio of Li2O to R2O in the range from about 0.45 to about 1; a difference between a total amount of R2O to the amount of Al2O3 in the range from about −5 to about 0; a difference between a total amount of RxO (in mol %) and the amount of Al2O3 in the range from about 0 to about 3; and a ratio of the amount of MgO (in mol %) to a total amount of RO (in mol %) in the range from about 0 to about 1. In one or more embodiments, the glass substrate is substantially free of nucleating agents.
An ninth aspect of this disclosure pertains to a glass substrate that includes in mol %, SiO2 in an amount in the range from about 68 to about 75; Al2O3 in an amount in the range from about 12 to about 15; B2O3 in an amount in the range from about 0.5 to about 5; Li2O in an amount in the range from about 2 to about 10; Na2O in an amount in the range from about 0 to about 6; MgO in an amount in the range from about 1 to about 4; ZnO in an amount in the range from about 0 to about 3; and CaO in an amount in the range from about 0 to about 5, wherein the glass substrate is amorphous and is strengthened. In one or more embodiments, the Na2O concentration varies in the glass substrate. In one or more embodiments, the glass substrate is substantially free of nucleating agents. In accordance with one or more embodiments, the strengthened glass substrate exhibits any one or more of the following compositional relationships: a ratio of Li2O to R2O in the range from about 0.45 to about 1; a difference between a total amount of R2O to the amount of Al2O3 in the range from about −5 to about 0; a difference between a total amount of RxO (in mol %) and the amount of Al2O3 in the range from about 0 to about 3; and a ratio of the amount of MgO (in mol %) to a total amount of RO (in mol %) in the range from about 0 to about 1.
A tenth aspect of this disclosure pertains to a device comprising: a housing having front, back, and side surfaces; electrical components that are at least partially inside the housing; a display at or adjacent to the front surface of the housing; and a cover substrate disposed over the display, wherein the cover substrate comprises a glass-based article according to the embodiments described herein.
Additional features and advantages will be set forth in the detailed description which follows, and in part will be readily apparent to those skilled in the art from that description or recognized by practicing the embodiments as described herein, including the detailed description which follows, the claims, as well as the appended drawings.
It is to be understood that both the foregoing general description and the following detailed description are merely exemplary and are intended to provide an overview or framework to understanding the nature and character of the claims. The accompanying drawings are included to provide a further understanding and are incorporated in and constitute a part of this specification. The drawings illustrate one or more embodiment(s), and together with the description serve to explain principles and operation of the various embodiments.
Reference will now be made in detail to various embodiments, examples of which are illustrated in the accompanying examples and drawings.
In the following description, like reference characters designate like or corresponding parts throughout the several views shown in the figures. It is also understood that, unless otherwise specified, terms such as “top,” “bottom,” “outward,” “inward,” and the like are words of convenience and are not to be construed as limiting terms. In addition, whenever a group is described as comprising at least one of a group of elements and combinations thereof, it is understood that the group may comprise, consist essentially of, or consist of any number of those elements recited, either individually or in combination with each other. Similarly, whenever a group is described as consisting of at least one of a group of elements or combinations thereof, it is understood that the group may consist of any number of those elements recited, either individually or in combination with each other. Unless otherwise specified, a range of values, when recited, includes both the upper and lower limits of the range as well as any ranges therebetween. As used herein, the indefinite articles “a,” “an,” and the corresponding definite article “the” mean “at least one” or “one or more,” unless otherwise specified. It also is understood that the various features disclosed in the specification and the drawings can be used in any and all combinations.
As used herein, the terms “glass-based article” and “glass-based substrates” are used in their broadest sense to include any object made wholly or partly of glass. Glass-based articles include laminates of glass and non-glass materials, laminates of glass and crystalline materials, and glass-ceramics (including an amorphous phase and a crystalline phase). Unless otherwise specified, all compositions are expressed in terms of mole percent (mol %).
It is noted that the terms “substantially” and “about” may be utilized herein to represent the inherent degree of uncertainty that may be attributed to any quantitative comparison, value, measurement, or other representation. These terms are also utilized herein to represent the degree by which a quantitative representation may vary from a stated reference without resulting in a change in the basic function of the subject matter at issue.
As used herein, the term “about” means that amounts, sizes, formulations, parameters, and other quantities and characteristics are not and need not be exact, but may be approximate and/or larger or smaller, as desired, reflecting tolerances, conversion factors, rounding off, measurement error and the like, and other factors known to those of skill in the art. When the term “about” is used in describing a value or an end-point of a range, the disclosure should be understood to include the specific value or end-point referred to. Whether or not a numerical value or end-point of a range in the specification recites “about,” the numerical value or end-point of a range is intended to include two embodiments: one modified by “about,” and one not modified by “about.” It will be further understood that the endpoints of each of the ranges are significant both in relation to the other endpoint, and independently of the other endpoint.
Unless otherwise specified, all temperatures are expressed in terms of degrees Celsius (° C.). As used herein the term “softening point” refers to the temperature at which the viscosity of a glass is approximately 107.6 poise (P), the term “anneal point” refers to the temperature at which the viscosity of a glass is approximately 1013.2 poise, the term “200 poise temperature (T200P)” refers to the temperature at which the viscosity of a glass is approximately 200 poise, the term “1011 poise temperature” refers to the temperature at which the viscosity of a glass is approximately 1011 poise, the term “35 kP temperature (T35kP)” refers to the temperature at which the viscosity of a glass is approximately 35 kilopoise (kP), and the term “160 kP temperature (T160kP)” refers to the temperature at which the viscosity of a glass is approximately 160 kP.
Referring to the drawings in general and to
As used herein, DOC refers to the depth at which the stress within the glass-based article changes compressive to tensile stress. At the DOC, the stress crosses from a positive (compressive) stress to a negative (tensile) stress (e.g., 130 in
As used herein, the terms “chemical depth”, “chemical depth of layer” and “depth of chemical layer” may be used interchangeably and refer to the depth at which an ion of the metal oxide or alkali metal oxide (e.g., the metal ion or alkali metal ion) diffuses into the glass-based article and the depth at which the concentration of the ion reaches a minimum value, as determined by Electron Probe Micro-Analysis (EPMA) or Glow Discharge-Optical Emission Spectroscopy (GD-OES)). In particular, to assess the depth of Na2O diffusion or Na+ ion concentration may be determined using EPMA and a surface stress meter (described in more detail below).
According to the convention normally used in the art, compression is expressed as a negative (<0) stress and tension is expressed as a positive (>0) stress, unless specifically noted otherwise. Throughout this description, however, when speaking in terms of compressive stress CS, such is given without regard to positive or negative values—i.e., as recited herein, CS=|CS|.
Described herein are thin, chemically strengthened glass-based articles that include glasses, such as silicate glasses including alkali-containing glass, and glass-ceramics that may be used as a cover glass for mobile electronic devices and touch-enabled displays. The glass-based articles may also be used in displays (or as display articles) (e.g., billboards, point of sale systems, computers, navigation systems, and the like), architectural articles (walls, fixtures, panels, windows, etc.), transportation articles (e.g., in automotive applications, trains, aircraft, sea craft, etc.), appliances (e.g., washers, dryers, dishwashers, refrigerators and the like), or any article that requires some fracture resistance.
In particular, the glass-based articles described herein are thin and exhibit stress profiles that are typically only achievable through tempering thick glass articles (e.g., having a thickness of about 2 mm or 3 mm or greater). The glass-based articles exhibit unique stress profiles along the thickness thereof. In some cases, the glass-based articles described herein exhibit a greater surface CS than tempered glass articles. In one or more embodiments, the glass-based articles have a compressive stress layer that extends deeper into the glass-based article (in which the CS decreases and increases more gradually than known chemically strengthened glass-based articles) such the glass-based article exhibits substantially improved fracture resistance, even when the glass-based article or a device including the same is dropped on a hard surface (e.g., granite) or a hard and rough surface (e.g., asphalt). The glass-based articles of one or more embodiments exhibit a greater maximum CT value than some known chemically strengthened glass substrates.
CS and depth of penetration of potassium ions (“Potassium DOL”) are measured using those means known in the art. Potassium DOL is distinguished from DOC because it represents the depth of potassium penetration as a result of an ion exchange process. Potassium DOL is typically less than the DOC for the articles described herein. CS and Potassium DOL are measured by surface stress meter (FSM) using commercially available instruments such as the FSM-6000, manufactured by Orihara Industrial Co., Ltd. (Japan). Surface stress measurements rely upon the accurate measurement of the stress optical coefficient (SOC), which is related to the birefringence of the glass. SOC in turn is measured according to a modified version of Procedure C described in ASTM standard C770-98 (2013), entitled “Standard Test Method for Measurement of Glass Stress-Optical Coefficient,” the contents of which are incorporated herein by reference in their entirety. The modification includes using a glass disc as the specimen with a thickness of 5 to 10 mm and a diameter of 12.7 mm, wherein the disc is isotropic and homogeneous and core drilled with both faces polished and parallel. The modification also includes calculating the maximum force, Fmax to be applied. The force should be sufficient to produce 20 MPa or more compression stress. Fmax is calculated as follows:
Fmax=7.854*D*h
DOC and maximum CT values are measured using a scattered light polariscope (SCALP) techniques known in the art. Refracted near-field (RNF) method or SCALP may be used to measure the stress profile. When the RNF method is utilized, the maximum CT value provided by SCALP is utilized. In particular, the stress profile measured by RNF is force balanced and calibrated to the maximum CT value provided by a SCALP measurement. The RNF method is described in U.S. Pat. No. 8,854,623, entitled “Systems and methods for measuring a profile characteristic of a glass sample”, which is incorporated herein by reference in its entirety. In particular, the RNF method includes placing the glass-based article adjacent to a reference block, generating a polarization-switched light beam that is switched between orthogonal polarizations at a rate of between 1 Hz and 50 Hz, measuring an amount of power in the polarization-switched light beam and generating a polarization-switched reference signal, wherein the measured amounts of power in each of the orthogonal polarizations are within 50% of each other. The method further includes transmitting the polarization-switched light beam through the glass sample and reference block for different depths into the glass sample, then relaying the transmitted polarization-switched light beam to a signal photodetector using a relay optical system, with the signal photodetector generating a polarization-switched detector signal. The method also includes dividing the detector signal by the reference signal to form a normalized detector signal and determining the profile characteristic of the glass sample from the normalized detector signal. The RNF profile is then smoothed and used for the CT region. As noted above, the FSM technique is used for the surface CS and slope of the stress profile in the CS region near the surface.
As stated above, the glass-based articles described herein are chemically strengthened by ion exchange and exhibit stress profiles that are distinguished from those exhibited by known strengthened glass articles. In this disclosure glass-based substrates are generally unstrengthened and glass-based articles generally refer to glass-based substrates that have been strengthened (by, for example, ion exchange). In this process, ions at or near the surface of the glass-based article are replaced by—or exchanged with—larger ions having the same valence or oxidation state. In those embodiments in which the glass-based article comprises an alkali aluminosilicate glass, ions in the surface layer of the glass and the larger ions are monovalent alkali metal cations, such as Li+ (when present in the glass-based article), Na+, K+, Rb+, and Cs+. Alternatively, monovalent cations in the surface layer may be replaced with monovalent cations other than alkali metal cations, such as Ag+ or the like. In such embodiments, the monovalent ions (or cations) exchanged into the glass-based substrate generate a stress in the resulting glass-based article.
Ion exchange processes are typically carried out by immersing a glass-based substrate in a molten salt bath (or two or more molten salt baths) containing the larger ions to be exchanged with the smaller ions in the glass-based substrate. It should be noted that aqueous salt baths may also be utilized. In addition, the composition of the bath(s) may include more than one type of larger ion (e.g., Na+ and K+) or a single larger ion. It will be appreciated by those skilled in the art that parameters for the ion exchange process, including, but not limited to, bath composition and temperature, immersion time, the number of immersions of the glass-based article in a salt bath (or baths), use of multiple salt baths, additional steps such as annealing, washing, and the like, are generally determined by the composition of the glass-based article (including the structure of the article and any crystalline phases present) and the desired DOC and CS of the glass-based article that results from strengthening. By way of example, ion exchange of glass-based substrates may be achieved by immersion of the glass-based substrates in at least one molten bath containing a salt such as, but not limited to, nitrates, sulfates, and chlorides of the larger alkali metal ion. Typical nitrates include KNO3, NaNO3, LiNO3, NaSO4 and combinations thereof. The temperature of the molten salt bath typically is in a range from about 380° C. up to about 450° C., while immersion times range from about 15 minutes up to about 100 hours depending on glass thickness, bath temperature and glass (or monovalent ion) diffusivity. However, temperatures and immersion times different from those described above may also be used.
In one or more embodiments, the glass-based substrates may be immersed in a molten salt bath of 100% NaNO3 having a temperature from about 370° C. to about 480° C. In some embodiments, the glass-based substrate may be immersed in a molten mixed salt bath including from about 5% to about 90% KNO3 and from about 10% to about 95% NaNO3. In some embodiments, the glass-based substrate may be immersed in a molten mixed salt bath including Na2SO4 and NaNO3 and have a wider temperature range (e.g., up to about 500° C.). In one or more embodiments, the glass-based article may be immersed in a second bath, after immersion in a first bath. Immersion in a second bath may include immersion in a molten salt bath including 100% KNO3 for 15 minutes to 8 hours.
In one or more embodiments, the glass-based substrate may be immersed in a molten, mixed salt bath including NaNO3 and KNO3 (e.g., 49%/51%, 50%/50%, 51%/49%) having a temperature less than about 420° C. (e.g., about 400° C. or about 380° C.). for less than about 5 hours, or even about 4 hours or less.
Ion exchange conditions can be tailored to provide a “spike” or to increase the slope of the stress profile at or near the surface of the resulting glass-based article. This spike can be achieved by single bath or multiple baths, with the bath(s) having a single composition or mixed composition, due to the unique properties of the glass compositions used in the glass-based articles described herein.
As illustrated in
The glass-based article includes a stress profile that extends from the first surface 302 to the second surface 304 (or along the entire length of the thickness t). In the embodiment shown in
As illustrated in
The surface CS 310 may be about 150 MPa or greater or about 200 MPa or greater (e.g., about 250 MPa or greater, about 300 MPa or greater, about 400 MPa or greater, about 450 MPa or greater, about 500 MPa or greater, or about 550 MPa or greater). The surface CS 310 may be up to about 900 MPa, up to about 1000 MPa, up to about 1100 MPa, or up to about 1200 MPa. The surface CS values herein may also comprise the maximum CS. In some embodiments, the surface CS is less than the maximum CS.
The maximum CT 320 may be greater than or equal to about 71.5/√(t). In some embodiments, the maximum CT 320 is about 80 MPa or greater, about 85 MPa or greater or about 90 MPa or greater. In some embodiments, the maximum CT 320 may be in the range from greater than about 80 MPa to about 100 MPa (e.g., from about 85 MPa to about 100 MPa, from about 90 MPa to about 100 MPa, from about 80 MPa to about 95 MPa, from about 80 MPa to about 90 MPa, from about 85 MPa to about 95 MPa, or from about 88 MPa to about 92 MP). The maximum CT 320 may be positioned at a range from about 0.3·t to about 0.7·t, from about 0.4·t to about 0.6·t or from about 0.45·t to about 0.55·t. It should be noted that any one or more of surface CS 310 and maximum CT 320 may be dependent on the thickness of the glass-based article. For example, glass-based articles having at thickness of about 0.8 mm may have a maximum CT in the range from about 85 MPa to about 100 MPa. When the thickness of the glass-based article decreases, the maximum CT may increase. In other words, the maximum CT increases with decreasing thickness (or as the glass-based article becomes thinner).
In some embodiments, the ratio of the maximum CT 320 to the surface CS 310 in the range from about 0.1 to about 0.8 (e.g., in the range from about 0.1 to about 0.7, from about 0.1 to about 0.6, from about 0.1 to about 0.5, from about 0.1 to about 0.4, from about 0.1 to about 0.3, from about 0.1 to about 0.25, from about 0.1 to about 0.2, from about 0.15 to about 0.8, from about 0.2 to about 0.8, from about 0.3 to about 0.8, from about 0.4 to about 0.8, from about 0.5 to about 0.8, or from about 0.6 to about 0.8). In known chemically strengthened glass-based articles, the ratio of the maximum CT 320 to the surface CS 310 is 0.1 or less. In some embodiments, surface CS may be 4 times (e.g., 5 times, 6 times or 6.5 times) the maximum CT or greater. In some embodiments, the surface CS may be up to about 47.5 times the maximum CT. The surface CS may be in the range from about 4 times up to about 7.5 times the maximum CT.
In one or more embodiments, the stress profile 312 comprises a maximum CS, which is typically the surface CS 310 and can be found at one or both of the first surface 302 and the second surface 304. In one or more embodiments, the CS layer or region 315 extends along a portion of the thickness 317 to the DOC 330 and a maximum CT 320. In one or more embodiments, the DOC 330 may be about 0.1·t or greater. For example, the DOC 330 may be about 0.12·t or greater, about 0.14·t or greater, about 0.15·t or greater, about 0.16·t or greater, 0.17·t or greater, 0.18·t or greater, 0.19·t or greater, 0.20·t or greater, about 0.21·t or greater, or up to about 0.25·t. In some embodiments, the DOC 330 is less than the chemical depth. The chemical depth may be about 0.4·t or greater, 0.5·t or greater, about 55·t or greater, or about 0.6·t or greater.
In one or more embodiments, the glass-based article comprises a potassium DOL in the range from about 6 micrometers to about 20 micrometers. In some embodiments, the potassium DOL may be expressed as a function of the thickness t of the glass-based article. In one or more embodiments, potassium DOL may be in the range from about 0.005t to about 0.05t. In some embodiments, the potassium DOL may be in the range from about 0.005t to about 0.05t, from about 0.005t to about 0.045t, from about 0.005t to about 0.04t, from about 0.005t to about 0.035t, from about 0.005t to about 0.03t, from about 0.005t to about 0.025t, from about 0.005t to about 0.02t, from about 0.005t to about 0.015t, from about 0.005t to about 0.01t, from about 0.006t to about 0.05t, from about 0.008t to about 0.05t, from about 0.01t to about 0.05t, from about 0.015t to about 0.05t, from about 0.02t to about 0.05t, from about 0.025t to about 0.05t, from about 0.03t to about 0.05t, or from about 0.01t to about 0.02t.
In one or more embodiments, the compressive stress value at the potassium DOL depth may be in the range from about 50 MPa to about 300 MPa. In some embodiments, the compressive stress value at the potassium DOL depth may be in the range from about 50 MPa to about 280 MPa, from about 50 MPa to about 260 MPa, from about 50 MPa to about 250 MPa, from about 50 MPa to about 240 MPa, from about 50 MPa to about 220 MPa, from about 50 MPa to about 200 MPa, from about 60 MPa to about 300 MPa, from about 70 MPa to about 300 MPa, from about 75 MPa to about 300 MPa, from about 80 MPa to about 300 MPa, from about 90 MPa to about 300 MPa, from about 100 MPa to about 300 MPa, from about 1100 MPa to about 300 MPa, from about 120 MPa to about 300 MPa, from about 130 MPa to about 300 MPa, or from about 150 MPa to about 300 MPa.
In one or more embodiments, the stress profile 312 may be described as parabolic-like in shape. In some embodiments, the stress profile along the region or depth of the glass-based article exhibiting tensile stress exhibits a parabolic-like shape. In one or more specific embodiments, the stress profile 312 is free of a flat stress (either compressive or tensile) portion or a portion that exhibits a substantially constant stress (either compressive or tensile). In some embodiments, the CT region exhibits a stress profile that is substantially free of a flat stress or free of a substantially constant stress. In one or more embodiments, all points of the stress profile 312 between a thickness range from about 0t up to about 0.2·t and greater than 0.8·t (or from about 0·t to about 0.3·t and greater than about 0.7·t up to t) comprise a tangent having a slope with an absolute value that is greater than about 0.1 MPa/micrometer. In some embodiments, the slope of the tangent may have an absolute value of greater than about 0.2 MPa/micrometer. In some more specific embodiments, the slope of the tangent may have an absolute value of greater than 0.3 MPa/micrometer. In even more specific embodiments, the slope of the tangent may have an absolute value of greater than 0.5 MPa/micrometer. In other words, the stress profile of one or more embodiments along these thickness ranges (i.e., 0·t up to about 0.2·t and greater than 0.8t, or from about 0t to about 0.3·t and about 0.7·t or greater) exclude points having a tangent with zero slope, or slope approximating zero, or flat slope. Without being bound by theory, known error function or quasi-linear stress profiles have points along these thickness ranges (i.e., from about 0·t up to about 0.2·t and greater than 0.8·t, or from about 0·t to about 0.3·t and about 0.7·t or greater) that have a tangent with a slope of zero or of a value that is close to zero, i.e., that may have an absolute value of less than about 0.1 MPa/micrometer (indicating a flat or zero slope stress profile along such thickness ranges, as shown in
In one or more embodiments, the glass-based article exhibits a stress profile in a thickness range from about 0.1·t to 0.3·t and from about 0.7·t to 0.9·t that comprises a tangent with a maximum slope and a minimum slope. In some instances, the difference between the maximum slope and the minimum slope is about 3.5 MPa/micrometers or less, about 3 MPa/micrometers or less, about 2.5 MPa/micrometers or less, or about 2 MPa/micrometers or less.
In one or more embodiments, the glass-based article includes a stress profile 312 that is substantially free of any flat segments that extend in a depth direction or along at least a portion of the thickness t of the glass-based article. In other words, the stress profile 312 is substantially continuously increasing or decreasing along the thickness t. In some embodiments, the stress profile is substantially free of any flat segments in a depth direction having a length of about 10 micrometers or more, about 50 micrometers or more, or about 100 micrometers or more, or about 200 micrometers or more. As used herein, the term “flat” refers to a slope having a magnitude of less than about 0.5 MPa/micrometer, or less than about 0.2 MPa/micrometer along the flat segment. In some embodiments, one or more portions of the stress profile that are substantially free of any flat segments in a depth direction are present at depths within the glass-based article of about 5 micrometers or greater (e.g., 10 micrometers or greater, or 15 micrometers or greater) from either one or both the first surface or the second surface. For example, along a depth of about 0 micrometers to less than about 5 micrometers from the first surface, the stress profile may include linear segments, but from a depth of about 5 micrometers or greater from the first surface, the stress profile may be substantially free of flat segments. As used herein “linear” includes line segments having flat slope as well as line segments not having flat slopes; for example of the latter, see
In some embodiments, the stress profile may include linear segments at depths from about 0t up to about 0.1t and may be substantially free of flat segments at depths of about 0.1t to about 0.4t. In some embodiments, the stress profile for a thickness in the range from about Otto about 0. It may have a slope whose magnitude (in absolute value) is in the range from about 20 MPa/micron to about 200 MPa/micron. As will be described herein, such embodiments may be formed using a single ion-exchange process by which the bath includes two or more alkali salts or is a mixed alkali salt bath or multiple (e.g., 2 or more) ion exchange processes.
In one or more embodiments, the glass-based article may be described in terms of the shape of the stress profile along the CT region (327 in
Stress(x)=MaxT−(((CTn·(n+1))/0.5n)·|(x/t)−0.5|n) (1)
In Equation (1), the stress (x) is the stress value at position x. Here the stress is positive (tension). In Equation (1), MaxT is the maximum tension value and CTn is the tension value at n and is less than or equal to MaxT. Both MaxT and CTn are positive values in units of MPa. The value x is position along the thickness (t) in micrometers, with a range from 0 to t; x=0 is one surface (302, in
In one or more embodiments, CTn may be less than MaxT where there is a compressive stress spike on one or both major surfaces of the glass-based article. In one or more embodiments, CTn is equal to MaxT when there is no compressive stress spike on one or both major surfaces of the glass-based article.
In some embodiments, the stress profile may be modified by heat treatment. In such embodiments, the heat treatment may occur before any ion-exchange processes, between ion-exchange processes, or after all ion-exchange processes. In some embodiments, the heat treatment may reduce the absolute value of the magnitude of the slope of the stress profile at or near the surface. In some embodiments, where a steeper or greater slope is desired at the surface, an ion-exchange process after the heat treatment may be utilized to provide a “spike” or to increase the slope of the stress profile at or near the surface.
In one or more embodiments, the stress profile 312 is generated due to a non-zero concentration of a metal oxide(s) that varies along a portion of the thickness. As mentioned above, the variation in metal oxide concentration may be referred to herein as a metal oxide concentration gradient. In some embodiments, the concentration of a metal oxide is non-zero and varies, both along a thickness range from about 0·t to about 0.3·t. In some embodiments, the concentration of the metal oxide is non-zero and varies along a thickness range from about 0·t to about 0.35·t, from about 0·t to about 0.4·t, from about 0·t to about 0.45·t or from about 0·t to about 0.48·t. The metal oxide may be described as generating a stress in the glass-based article. The variation in concentration may be continuous along the above-referenced thickness ranges. Variation in concentration may include a change in metal oxide concentration of about 0.2 mol % along a thickness segment of about 100 micrometers. This change may be measured by known methods in the art including microprobe, as shown in Example 1. The metal oxide that is non-zero in concentration and varies along a portion of the thickness may be described as generating a stress in the glass-based article.
The variation in concentration may be continuous along the above-referenced thickness ranges. In some embodiments, the variation in concentration may be continuous along thickness segments in the range from about 10 micrometers to about 30 micrometers. In some embodiments, the concentration of the metal oxide decreases from the first surface to a value at a point between the first surface and the second surface and increases from the value to the second surface.
The concentration of metal oxide may include more than one metal oxide (e.g., a combination of Na2O and K2O). In some embodiments, where two metal oxides are utilized and where the radius of the ions differ from one or another, the concentration of ions having a larger radius is greater than the concentration of ions having a smaller radius at shallow depths, while the at deeper depths, the concentration of ions having a smaller radius is greater than the concentration of ions having larger radius. For example, where a single Na- and K-containing bath is used in the ion exchange process, the concentration of K+ ions in the glass-based article is greater than the concentration of Na+ ions at shallower depths, while the concentration of Na+ is greater than the concentration of K+ ions at deeper depths. This is due, in part, due to the size of the monovalent ions that are exchanged into the glass for smaller monovalent ions. In such glass-based articles, the area at or near the surface comprises a greater CS due to the greater amount of larger ions (i.e., K+ ions) at or near the surface. This greater CS may be exhibited by a stress profile having a steeper slope at or near the surface (i.e., a spike in the stress profile at the surface).
The concentration gradient or variation of one or more metal oxides is created by chemically strengthening a glass-based substrate, as previously described herein, in which a plurality of first metal ions in the glass-based substrate is exchanged with a plurality of second metal ions. The first ions may be ions of lithium, sodium, potassium, and rubidium. The second metal ions may be ions of one of sodium, potassium, rubidium, and cesium, with the proviso that the second alkali metal ion has an ionic radius greater than the ionic radius of the first alkali metal ion. The second metal ion is present in the glass-based substrate as an oxide thereof (e.g., Na2O, K2O, Rb2O, Cs2O or a combination thereof).
In one or more embodiments, the metal oxide concentration gradient extends through a substantial portion of the thickness t or the entire thickness t of the glass-based article, including the CT layer 327. In one or more embodiments, the concentration of the metal oxide is about 0.5 mol % or greater in the CT layer 327. In some embodiments, the concentration of the metal oxide may be about 0.5 mol % or greater (e.g., about 1 mol % or greater) along the entire thickness of the glass-based article and is greatest at the first surface 302 and/or the second surface 304 and decreases substantially constantly to a value at a point between the first surface 302 and the second surface 304. At that point, the concentration of the metal oxide is the least along the entire thickness t; however, the concentration is also non-zero at that point. In other words, the non-zero concentration of that particular metal oxide extends along a substantial portion of the thickness t (as described herein) or the entire thickness t. In some embodiments, the lowest concentration in the particular metal oxide is in the CT layer 327. The total concentration of the particular metal oxide in the glass-based article may be in the range from about 1 mol % to about 20 mol %.
In one or more embodiments, the glass-based article includes a first metal oxide concentration and a second metal oxide concentration, such that the first metal oxide concentration is in the range from about 0 mol % to about 15 mol % along a first thickness range from about 0t to about 0.5t, and the second metal oxide concentration is in the range from about 0 mol % to about 10 mol % from a second thickness range from about 0 micrometers to about 25 micrometers (or from about 0 micrometers to about 12 micrometers); however, the concentration of one or both the first metal oxide and the second metal oxide is non-zero along a substantial portion or the entire thickness of the glass-based article. The glass-based article may include an optional third metal oxide concentration. The first metal oxide may include Na2O while the second metal oxide may include K2O.
The concentration of the metal oxide may be determined from a baseline amount of the metal oxide in the glass-based article prior to being modified to include the concentration gradient of such metal oxide.
In one or more embodiments, the glass-based articles may be described in terms of how they fracture and the fragments that result from such fracture, as measured by the “Frangibility Test”, as described Z. Tang, et al. Automated Apparatus for Measuring the Frangibility and Fragmentation of Strengthened Glass. Experimental Mechanics (2014) 54:903-912. In one or more embodiments, when fractured, the glass-based articles fracture into 2 or more fragments per square inch (or per 6.4516 square centimeters) of the glass-based article (prior to fracture). In some cases, the glass-based articles fracture into 3 or more, 4 or more, 5 or more, or 10 or more fragments per square inch (or per 6.4516 square centimeters) of the glass-based article (prior to fracture). In some instances, when fractured, the glass-based articles fracture into fragments such that 50% or more of the fragments have a surface area that is less than 5%, less than 2%, or less than 1% of the surface area of the glass-based article (prior to fracture), and the sample size used was 5.08 cm by 5.08 cm (2 inch by 2 inch) square. In some embodiments, when fractured, the glass-based articles fracture into fragments such that 90% or more or even 100% of the fragments have a surface area that is less than 5%, less than 2%, or less than 1% of the surface area of the glass-based article (prior to fracture).
In one or more embodiments, after chemically strengthening the glass-based article, the resulting stress profile 312 of the glass-based article provides improved fracture resistance. For example, in some embodiments, upon fracture, the glass-based article comprises fragments having an average longest cross-sectional dimension of less than or equal to about 2·t (e.g., 1.8·t, 1.6·t, 1.5·t, 1.4·t, 1.2·t or 1.·t or less) as measured by the “Frangibility Test”, as described Z. Tang, et al. Automated Apparatus for Measuring the Frangibility and Fragmentation of Strengthened Glass. Experimental Mechanics (2014) 54:903-912. The number of fragments is divided by the area of the sample being tested (in square inches), and the sample size used was 5.08 cm by 5.08 cm (2 inch by 2 inch) square.
In one or more embodiments, the glass-based articles may exhibit a fracture toughness (K1C) of about 0.65 MPa·m1/2 or greater. In some cases, the fracture toughness may be about 0.69 MPa·m1/2 or greater, about 0.7 MPa·m1/2 or greater, about 0.8 MPa·m1/2 or greater, or about 0.9 MPa·m1/2 or greater. In some embodiments the fracture toughness may be in the range from about 0.65 MPa·m1/2 to about 1 MPa·m1/2. The fracture toughness value (K1C) recited in this disclosure refers to a value as measured by chevron notched short bar (CNSB) method disclosed in Reddy, K. P. R. et al, “Fracture Toughness Measurement of Glass and Ceramic Materials Using Chevron-Notched Specimens,” J. Am. Ceram. Soc., 71 [6], C-310-C-313 (1988) except that Y*m is calculated using equation 5 of Bubsey, R. T. et al., “Closed-Form Expressions for Crack-Mouth Displacement and Stress Intensity Factors for Chevron-Notched Short Bar and Short Rod Specimens Based on Experimental Compliance Measurements,” NASA Technical Memorandum 83796, pp. 1-30 (October 1992).
In some embodiments, the substrate may also be characterized as having a hardness from about 500 HVN to about 800 HVN (kgf/mm2), as measured by Vicker's hardness test at a load of 200 g. In some embodiments, the glass-based article may include a Vicker's hardness is in the range from about 600 HVN to about 800 HVN.
The glass-based articles described herein may exhibit a stored tensile energy in the range from greater than 0 J/m2 to about 40 J/m2. In some instances, the stored tensile energy may be in the range from about 5 J/m2 to about 40 J/m2, from about 10 J/m2 to about 40 J/m2, from about 15 J/m2 to about 40 J/m2, from about 20 J/m2 to about 40 J/m2, from about 1 J/m2 to about 35 J/m2, from about 1 J/m2 to about 30 J/m2, from about 1 J/m2 to about 25 J/m2, from about 1 J/m2 to about 20 J/m2, from about 1 J/m2 to about 15 J/m2, from about 1 J/m2 to about 10 J/m2, from about 10 J/m2 to about 30 J/m2, from about 10 J/m2 to about 25 J/m2, from about 15 J/m2 to about 30 J/m2, from about 15 J/m2 to about 25 J/m2, from about 18 J/m2 to about 22 J/m2, from about 25 J/m2 to about 40 J/m2, or from about 25 J/m2 to about 30 J/m2. The thermally and chemically strengthened glass-based articles of one or more embodiments may exhibit a stored tensile energy of about 6 J/m2 or greater, about 10 J/m2 or greater, about 15 J/m2 or greater, or about 20 J/m2 or greater.
Stored tensile energy may be calculated using the following Equation (2):
stored tensile energy(J/m2)=[(1−ν)/E]∫(σ{circumflex over ( )}2)(dt) (2)
where ν is Poisson's ratio, E is the Young's modulus (in MPa), σ is stress (in MPa) and the integration is computed across the thickness (in microns) of the tensile region only. Each of the Young's modulus values recited in this disclosure refers to a value as 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 glass-based articles described herein generally have a Young's modulus of about 70 GPa or greater (e.g., in the range from about 70 GPa to about 100 GPa, from about 72 GPa to about 100 GPa, from about 75 GPa to about 100 GPa, from about 76 GPa to about 100 GPa, from about 78 GPa to about 100 GPa, from about 80 GPa to about 100 GPa, from about 82 GPa to about 100 GPa, from about 84 GPa to about 100 GPa, from about 86 GPa to about 100 GPa, from about 88 GPa to about 100 GPa, from about 90 GPa to about 100 GPa, from about 70 GPa to about 95 GPa, from about 70 GPa to about 90 GPa, from about 70 GPa to about 88 GPa, from about 70 GPa to about 86 GPa, from about 70 GPa to about 85 GPa, from about 70 GPa to about 84 GPa, from about 70 GPa to about 82 GPa, or from about 70 GPa to about 80 GPa). The Young's modulus, which is intrinsic to the composition of the glass-based article, can provide the desired high stiffness, which is an extrinsic property, to the ultimate glass-based article that is produced therefrom.
In some embodiments, the glass-based article comprises a low liquidus viscosity that enables the formation of the glass-based articles via thin rolling techniques. As used herein, the term “liquidus viscosity” refers to the viscosity of a molten glass at the liquidus temperature, wherein the term “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). In general, the glass-based articles (or the compositions used to form such articles) described herein a liquidus viscosity of less than about 100 kilopoise (kP). In some embodiments, the glass-based articles (or the compositions used to form such articles) exhibit a liquidus viscosity of less than about 80 kP, less than about 60 kP, less than about 40 kP, less than about 30 kP (e.g., in the range from about 15 kP to about 30 kP). The liquidus viscosity 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 liquidus temperature is measured in accordance with ASTM C965-96(2012), titled “Standard Practice for Measuring Viscosity of Glass Above the Softening Point”.
In one or more embodiments, the glass-based articles exhibit a Knoop Lateral Cracking Scratch Threshold in the range from about 4 N to about 7 N, from about 4.5 N to about 7 N, from about 5 N to about 7 N, from about 4 N to about 6.5 N, from about 4 N to about 6 N, or from about 5 N to about 6 N. As used herein, Knoop Scratch Lateral Cracking Threshold is the onset of lateral cracking (in 3 or more of 5 scratch events). A series of increasing constant load scratches (3 minimum per load, but more per load could be used to increase confidence level) are performed to identify the Knoop scratch threshold. In Knoop Scratch Lateral Cracking Threshold testing, for each load, samples of the glass substrates and/or articles were scratched with a Knoop indenter over a length of 10 mm with a velocity of 0.25 mm/s. The Knoop scratch threshold range can be determined by comparing the test specimen to one of the following 3 failure modes: 1) sustained lateral surface cracks that are more than two times the width of the groove, 2) damage is contained within the groove, but there are lateral surface cracks that are less than two times the width of groove and there is damage visible by naked eye, or 3) the presence of large subsurface lateral cracks which are greater than two times the width of the groove and/or there is a median crack at the vertex of the scratch. The scratch threshold is then the highest load at which failure does not occur in 3 or more of 5 events.
In one or more embodiments, the glass-based articles exhibit a Vicker's Indentation Fracture Threshold in the range from about 10 kgf or greater, about 12 kgf or greater, or about 15 kgf or greater. In some instances, the glass-based articles exhibit a Vicker's Indentation Fracture Threshold in the range from about 15 kgf to about 25 kgf. As used herein, Vicker's Indentation Fracture Threshold is the onset of median/radial cracking (in 3 or more of 5 indentation events) extending from at least one corner of the indentation site. In Vicker's Indentation Fracture Threshold testing, samples of the glass substrates and articles were repeatedly indented with a diamond tip (at 1360 angle) at increasing loads. Each indentation has the potential to produce 4 radial cracks, one from each corner of the indent. By counting the average number of radial cracks at each indentation load, the cracking threshold is the load at which there is an average of 2 cracks per indent (or the 50% cracking threshold).
In one or more embodiments, the glass-based articles exhibit improved surface strength when subjected to abraded ring-on-ring (AROR) testing. The strength of a material is the stress at which fracture occurs. The AROR test is a surface strength measurement for testing flat glass specimens, and ASTM C1499-09(2013), entitled “Standard Test Method for Monotonic Equibiaxial Flexural Strength of Advanced Ceramics at Ambient Temperature,” serves as the basis for the AROR test methodology described herein. The contents of ASTM C1499-09 are incorporated herein by reference in their entirety. In one embodiment, the glass specimen is abraded prior to ring-on-ring testing with 90 grit silicon carbide (SiC) particles that are delivered to the glass sample using the method and apparatus described in Annex A2, entitled “abrasion Procedures,” of ASTM C158-02(2012), entitled “Standard Test Methods for Strength of Glass by Flexure (Determination of Modulus of Rupture). The contents of ASTM C158-02 and the contents of Annex 2 in particular are incorporated herein by reference in their entirety.
Prior to ring-on-ring testing a surface of the glass-based article is abraded as described in ASTM C158-02, Annex 2, to normalize and/or control the surface defect condition of the sample using the apparatus shown in Figure A2.1 of ASTM C158-02. The abrasive material is typically sandblasted onto the surface 110 of the glass-based article at a load of 15 psi using an air pressure of 304 kPa (44 psi); although in the Examples below, the abrasive material was sandblasted onto the surface 110 at other loads (e.g., 25 psi or 45 psi). After air flow is established, 5 cm3 of abrasive material is dumped into a funnel and the sample is sandblasted for 5 seconds after introduction of the abrasive material.
For the AROR test, a glass-based article having at least one abraded surface 410 as shown in
The ratio of diameters of the loading ring and support ring D1/D2 may be in a range from about 0.2 to about 0.5. In some embodiments, D1/D2 is about 0.5. Loading and support rings 130, 120 should be aligned concentrically to within 0.5% of support ring diameter D2. The load cell used for testing should be accurate to within ±1% at any load within a selected range. In some embodiments, testing is carried out at a temperature of 23±2° C. and a relative humidity of 40±10%.
For fixture design, the radius r of the protruding surface of the loading ring 430, h/2≤r≤3h/2, where h is the thickness of glass-based article 410. Loading and support rings 430, 420 are typically made of hardened steel with hardness HRc>40. AROR fixtures are commercially available.
The intended failure mechanism for the AROR test is to observe fracture of the glass-based article 410 originating from the surface 430a within the loading ring 430. Failures that occur outside of this region—i.e., between the loading rings 430 and support rings 420—are omitted from data analysis. Due to the thinness and high strength of the glass-based article 410, however, large deflections that exceed 12 of the specimen thickness h are sometimes observed. It is therefore not uncommon to observe a high percentage of failures originating from underneath the loading ring 430. Stress cannot be accurately calculated without knowledge of stress development both inside and under the ring (collected via strain gauge analysis) and the origin of failure in each specimen. AROR testing therefore focuses on peak load at failure as the measured response.
The strength of glass-based article depends on the presence of surface flaws. However, the likelihood of a flaw of a given size being present cannot be precisely predicted, as the strength of glass is statistical in nature. A probability distribution can therefore generally be used as a statistical representation of the data obtained.
In some embodiments, the glass-based articles described herein have a surface or equibiaxial flexural strength of 20 kgf or more, and up to about 30 kgf as determined by AROR testing using a load of 25 psi or even 45 psi to abrade the surface. In other embodiments, the surface strength is 25 kgf or more, and in still other embodiments, 30 kgf or more.
In some embodiments, the glass-based articles described herein may be described in terms of performance in an inverted ball on sandpaper (IBoS) test. The IBoS test is a dynamic component level test that mimics the dominant mechanism for failure due to damage introduction plus bending that typically occurs in glass-based articles that are used in mobile or hand held electronic devices, as schematically shown in
An IBoS test apparatus is schematically shown in
Various materials may be used as the abrasive surface. In a one particular embodiment, the abrasive surface is sandpaper, such as silicon carbide or alumina sandpaper, engineered sandpaper, or any abrasive material known to those skilled in the art for having comparable hardness and/or sharpness. In some embodiments, sandpaper having 30 grit may be used, as it has a surface topography that is more consistent than either concrete or asphalt, and a particle size and sharpness that produces the desired level of specimen surface damage.
In one aspect, a method 600 of conducting the IBoS test using the apparatus 500 described hereinabove is shown in
In Step 520, a solid ball 530 of predetermined mass and size is dropped from a predetermined height h onto the upper surface of the glass-based article sample 518, such that the ball 530 impacts the upper surface (or adhesive tape 520 affixed to the upper surface) at approximately the center (i.e., within 1 mm, or within 3 mm, or within 5 mm, or within 10 mm of the center) of the upper surface. Following impact in Step 520, the extent of damage to the glass-based article sample 518 is determined (Step 630). As previously described hereinabove, herein, the term “fracture” means that a crack propagates across the entire thickness and/or entire surface of a substrate when the substrate is dropped or impacted by an object.
In method 600, the sheet 518 with the abrasive surface may be replaced after each drop to avoid “aging” effects that have been observed in repeated use of other types (e.g., concrete or asphalt) of drop test surfaces.
Various predetermined drop heights h and increments are typically used in method 600. The test may, for example, utilize a minimum drop height to start (e.g., about 10-20 cm). The height may then be increased for successive drops by either a set increment or variable increments. The test described in method 600 is stopped once the glass-based article sample 518 breaks or fractures (Step 631). Alternatively, if the drop height h reaches the maximum drop height (e.g., about 100 cm) without fracture, the drop test of method 300 may also be stopped, or Step 520 may be repeated at the maximum height until fracture occurs.
In some embodiments, IBoS test of method 600 is performed only once on each glass-based article sample 518 at each predetermined height h. In other embodiments, however, each sample may be subjected to multiple tests at each height.
If fracture of the glass-based article sample 518 has occurred (Step 631 in
When subjected to the inverted ball on sandpaper (IBoS) test described above, embodiments of the glass-based article described herein have about a 60% or more survival rate when the ball is dropped onto the surface of the glass from a height of 100 cm. For example, a glass-based article is described as having a 60% survival rate when dropped from a given height when three of five identical (or nearly identical) samples (i.e., having approximately the same composition and, when strengthened, approximately the same compressive stress and depth of compression or compressive stress layer, as described herein) survive the IBoS drop test without fracture when dropped from the prescribed height (here 100 cm). In other embodiments, the survival rate in the 80 cm IBoS test of the glass-based articles that are strengthened is about 70% or more, in other embodiments, about 80% or more, and, in still other embodiments, about 90% or more. In other embodiments, the survival rate of the strengthened glass-based articles dropped from a height of 100 cm in the IBoS test is about 60% or more, in other embodiments, about 70% or more, in still other embodiments, about 80% or more, and, in other embodiments, about 90% or more. In one or more embodiments, the survival rate of the strengthened glass-based articles dropped from a height of 150 cm in the IBoS test is about 60% or more, in other embodiments, about 70% or more, in still other embodiments, about 80% or more, and, in other embodiments, about 90% or more.
To determine the survivability rate of the glass-based articles when dropped from a predetermined height using the IBoS test method and apparatus described hereinabove, at least five identical (or nearly identical) samples (i.e., having approximately the same composition and, if strengthened, approximately the same compressive stress and depth of compression or layer) of the glass-based articles are tested, although larger numbers (e.g., 10, 20, 30, etc.) of samples may be subjected to testing to raise the confidence level of the test results. Each sample is dropped a single time from the predetermined height (e.g., 100 cm or 150 cm) or, alternatively, dropped from progressively higher heights without fracture until the predetermined height is reached, and visually (i.e., with the naked eye) examined for evidence of fracture (crack formation and propagation across the entire thickness and/or entire surface of a sample). A sample is deemed to have “survived” the drop test if no fracture is observed after being dropped from the predetermined height, and a sample is deemed to have “failed (or “not survived”) if fracture is observed when the sample is dropped from a height that is less than or equal to the predetermined height. The survivability rate is determined to be the percentage of the sample population that survived the drop test. For example, if 7 samples out of a group of 10 did not fracture when dropped from the predetermined height, the survivability rate of the glass would be 70%.
The glass-based articles described herein may be transparent. In one or more the glass-based article may have a thickness of about 3 millimeters or less, for example 1 millimeter or less, and exhibit a transmittance of about 88% or greater over a wavelength in the range from about 380 nm to about 780 nm.
The glass-based article may also exhibit a substantially white color. For example, the glass-based article may exhibit CIELAB color space coordinates, under a CIE illuminant F02, of L* values of about 88 and greater, a* values in the range from about −3 to about +3, and b* values in the range from about −6 to about +6. Alternatively, the glass-based article may exhibit CIELAB color space coordinates, under a CIE illuminant F02, of L* values of about 40 and less, a* values in the range from about −3 to about +3, and b* values in the range from about −6 to about +6. Such color space coordinates may be present under other CIE illuminants (e.g., D65).
Choice of substrates not particularly limited. In some examples, the glass-based article may be described as having a high cation diffusivity for ion exchange. In one or more embodiments, the glass or glass-ceramic has fast ion-exchange capability, i.e., the glass or glass-ceramic exhibits a monovalent ion diffusivity that is about 450 μm2/hour or greater at 460° C. or is about 500 μm2/hour or greater at 460° C. In one or more embodiments, the glass or glass-ceramic exhibits a sodium ion diffusivity that is about 450 μm2/hour or greater at 460° C. or is about 500 μm2/hour or greater at 460° C. In one or more embodiments, the glass or glass-ceramic exhibits a potassium ion diffusivity that is about 450 μm2/hour or greater at 460° C. or is about 500 μm2/hour or greater at 460° C.
The glass-based article may include an amorphous substrate, a crystalline substrate or a combination thereof (e.g., a glass-ceramic substrate). In one or more embodiments, the glass-based article substrate (prior to being chemically strengthened as described herein) may include a glass composition, in mole percent (mole %), including: SiO2 in the range from about 40 to about 80, Al2O3 in the range from about 10 to about 30, B2O3 in the range from about 0 to about 10, R2O in the range from about 0 to about 20, and RO in the range from about 0 to about 15. As used herein, R2O refers to the total amount of alkali metal oxides such as Li2O, Na2O, K2O, Rb2O, and Cs2O. As used herein RO refers to the total amount of alkaline earth metal oxides such as MgO, CaO, SrO, BaO, ZnO and the like. In some instances, the composition may include either one or both of ZrO2 in the range from about 0 mol % to about 5 mol % and P2O5 in the range from about 0 to about 15 mol %. TiO2 can be present from about 0 mol % to about 2 mol %.
In some embodiments, the glass composition may include SiO2 in an amount, in mol %, in the range from about 45 to about 80, from about 45 to about 75, from about 45 to about 70, from about 45 to about 65, from about 45 to about 60, from about 45 to about 65, from about 45 to about 65, from about 50 to about 70, from about 55 to about 70, from about 60 to about 70, from about 70 to about 75, from about 70 to about 72, or from about 50 to about 65.
In some embodiments, the glass composition may include Al2O3 in an amount, in mol %, in the range from about 5 to about 28, from about 5 to about 26, from about 5 to about 25, from about 5 to about 24, from about 5 to about 22, from about 5 to about 20, from about 6 to about 30, from about 8 to about 30, from about 10 to about 30, from about 12 to about 30, from about 12 to about 18, or from about 12 to about 14.
In one or more embodiments, the glass composition may include B2O3 in an amount, in mol %, in the range from about 0 to about 8, from about 0 to about 6, from about 0 to about 4, from about 0.1 to about 8, from about 0.1 to about 6, from about 0.1 to about 4, from about 1 to about 10, from about 2 to about 10, from about 4 to about 10, from about 2 to about 8, from about 0.1 to about 5, or from about 1 to about 3. In some instances, the glass composition may be substantially free of B2O3. As used herein, the phrase “substantially free” with respect to the components of the composition means that the component is not actively or intentionally added to the composition during initial batching, but may be present as an impurity in an amount less than about 0.001 mol %.
In some embodiments, the glass composition may include one or more alkali earth metal oxides, such as MgO, CaO and ZnO. In some embodiments, the total amount of the one or more alkali earth metal oxides may be a non-zero amount up to about 15 mol %. In one or more specific embodiments, the total amount of any of the alkali earth metal oxides may be a non-zero amount up to about 14 mol %, up to about 12 mol %, up to about 10 mol %, up to about 8 mol %, up to about 6 mol %, up to about 4 mol %, up to about 2 mol %, or up about 1.5 mol %. In some embodiments, the total amount, in mol %, of the one or more alkali earth metal oxides may be in the range from about 0.1 to 10, from about 0.1 to 8, from about 0.1 to 6, from about 0.1 to 5, from about 1 to 10, from about 2 to 10, or from about 2.5 to 8. The amount of MgO may be in the range from about 0 mol % to about 5 mol % (e.g., from about 2 mol % to about 4 mol %). The amount of ZnO may be in the range from about 0 to about 2 mol % (e.g., from about 0.1 mol % to about 2 mol %, from about 0.1 mol % to about 1 mol % or from about 0.5 mol % to about 1.5 mol %). The amount of CaO may be from about 0 mol % to about 2 mol %. In one or more embodiments, the glass composition may include MgO and may be substantially free of CaO and ZnO. In one variant, the glass composition may include any one of CaO or ZnO and may be substantially free of the others of MgO, CaO and ZnO. In one or more specific embodiments, the glass composition may include only two of the alkali earth metal oxides of MgO, CaO and ZnO and may be substantially free of the third of the earth metal oxides.
The total amount, in mol %, of alkali metal oxides R2O in the glass composition may be in the range from about 5 to about 20, from about 5 to about 18, from about 5 to about 16, from about 5 to about 15, from about 5 to about 14, from about 5 to about 12, from about 5 to about 10, from about 5 to about 8, from about 5 to about 20, from about 6 to about 20, from about 7 to about 20, from about 8 to about 20, from about 8 to about 18, from about 8 to about 16, from about 8 to about 14, from about 8 to about 12, or from about 8 to about 11.
In one or more embodiments, the glass composition includes Na2O in an amount in the range from about 0 mol % to about 18 mol %, from about 0 mol % to about 16 mol % or from about 0 mol % to about 14 mol %, from about 0 mol % to about 12 mol %, from about 1 mol % to about 18 mol %, from about 1 mol % to about 16 mol %, from about 1 mol % to about 14 mol %, from about 1 mol % to about 12 mol %, from about 1 mol % to about 10 mol %, from about 1 mol % to about 8 mol %, from about 1 mol % to about 5 mol %, from about 1 mol % to about 4 mol %, or from about 1 mol % to about 3 mol %. In some embodiments, the composition may include less than about 4 mol % Na2O.
In some embodiments, the amount of Li2O and Na2O is controlled to a specific amount or ratio to balance formability and ion exchangeability. For example, as the amount of Li2O increases, the liquidus viscosity may be reduced, thus preventing some forming methods from being used; however, such glass compositions are ion exchanged to deeper DOC levels, as described herein. The amount of Na2O can modify liquidus viscosity but can inhibit ion exchange to deeper DOC levels. In one or more embodiments, for sufficient stress at depth in Li2O containing glass compositions (or those compositions where an Na+ for Li+ exchange is the primary strengthening mechanism), the glass composition of one or more embodiments includes the compositional ratio of Li2O/(R2O) of greater than about 0.3, about 0.45 or greater, about 0.5 or greater, or about 0.7 or greater. To maintain higher CS values at deeper depths in the glass-based articles described herein, and especially in such glass-based articles that include Na2O (or those compositions where a K+ for Na+ exchange is the primary strengthening mechanism), the glass composition of one or more embodiments may include the compositional ratio of Na2O/(R2O) of greater than about 0.3, about 0.5 or greater, or about 0.7 or greater.
In one or more embodiments, the glass composition may include K2O in an amount less than about 5 mol %, less than about 4 mol %, less than about 3 mol %, less than about 2 mol %, or less than about 1 mol %. In one or more alternative embodiments, the glass composition may be substantially free, as defined herein, of K2O.
In one or more embodiments, the glass composition may include Li2O in an amount about 0 mol % to about 18 mol %, from about 0 mol % to about 15 mol % or from about 0 mol % to about 10 mol %, from about 0 mol % to about 8 mol %, from about 0 mol % to about 6 mol %, from about 0 mol % to about 4 mol % or from about 0 mol % to about 2 mol %. In some embodiments, the glass composition may include Li2O in an amount about 2 mol % to about 10 mol %, from about 4 mol % to about 10 mol %, from about 6 mol % to about 10 mol, or from about 5 mol % to about 8 mol %. In one or more alternative embodiments, the glass composition may be substantially free, as defined herein, of Li2O.
In one or more embodiments, the glass composition may include Fe2O3. In such embodiments, Fe2O3 may be present in an amount less than about 1 mol %, less than about 0.9 mol %, less than about 0.8 mol %, less than about 0.7 mol %, less than about 0.6 mol %, less than about 0.5 mol %, less than about 0.4 mol %, less than about 0.3 mol %, less than about 0.2 mol %, less than about 0.1 mol % and all ranges and sub-ranges therebetween. In one or more alternative embodiments, the glass composition may be substantially free, as defined herein, of Fe2O3.
In one or more embodiments, the glass composition may include ZrO2. In such embodiments, ZrO2 may be present in an amount less than about 1 mol %, less than about 0.9 mol %, less than about 0.8 mol %, less than about 0.7 mol %, less than about 0.6 mol %, less than about 0.5 mol %, less than about 0.4 mol %, less than about 0.3 mol %, less than about 0.2 mol %, less than about 0.1 mol % and all ranges and sub-ranges therebetween. In one or more alternative embodiments, the glass composition may be substantially free, as defined herein, of ZrO2.
In one or more embodiments, the glass composition may include P2O5 in a range from about 0 mol % to about 10 mol %, from about 0 mol % to about 8 mol %, from about 0 mol % to about 6 mol %, from about 0 mol % to about 4 mol %, from about 0.1 mol % to about 10 mol %, from about 0.1 mol % to about 8 mol %, from about 2 mol % to about 8 mol %, from about 2 mol % to about 6 mol % or from about 2 mol % to about 4 mol %. In some instances, the glass composition may be substantially free of P2O5.
In one or more embodiments, the glass composition may include TiO2. In such embodiments, TiO2 may be present in an amount less than about 6 mol %, less than about 4 mol %, less than about 2 mol %, or less than about 1 mol %. In one or more alternative embodiments, the glass composition may be substantially free, as defined herein, of TiO2. In some embodiments, TiO2 is present in an amount in the range from about 0.1 mol % to about 6 mol %, or from about 0.1 mol % to about 4 mol %.
In some embodiments, the glass composition may include various compositional relationships. For example, the glass composition may include a ratio of the amount of Li2O (in mol %) to the total amount of R2O (in mol %) in the range from about 0 to about 1, from about 0.4 to about 1, from about 0.45 to about 1, from about 0.5 to about 1, or from about 0.6 to about 1.
In some embodiments, the glass composition may include a difference between the total amount of R2O (in mol %) to the amount of Al2O3 (in mol %) (R2O—Al2O3) in the range from about −5 to about 2 (e.g., from about −5 to about 1.5, from about −5 to about 1, from about −5 to about 0, from about −5 to about −1, from about −5 to about −2, from about −4 to about 2, from about −3 to about 2, from about −2 to about 2 or from about −3 to about −1).
In some embodiments, the glass composition may include a difference between the total amount of RxO (in mol %) to the amount of Al2O3 (in mol %) (RxO-Al2O3) in the range from about 0 to about 5 (e.g., from about 0 to about 4, from about 0 to about 3, from about 0.1 to about 4, from about 0.1 to about 3, from about 1 to about 3, or from about 1 to about 2). As used herein, RxO includes R2O and RO, as defined herein.
In some embodiments, the glass composition may include a ratio of the total amount of R2O (in mol %) to the amount of Al2O3 (in mol %) (R2O/Al2O3) in the range from about −4 to about 5, from about −2 to about 4, or from about 0.1 to about 5. For example, the ratio of the total amount of R2O (in mol %) to the amount of Al2O3 (in mol %) (R2O/Al2O3) may be in the range from about −4 to about 4.5, from about −4 to about 4, from about −4 to about 3.5, from about −4 to about 3, from about −4 to about 2.5, from about −4 to about 2, from about −4 to about 1.5, from about −4 to about 1, from about −3.5 to about 5, from about −3 to about 5, from about −2.5 to about 5, from about −2 to about 5, from about −1.5 to about 5, from about −1 to about 5, from about 0 to about 5, from about 0 to about 4, from about 0 to about 3, from about 0.1 to about 4, from about 0.1 to about 3, or from about 0.1 to about 2.
In one or more embodiments, the glass composition includes a combined amount of Al2O3 and Na2O of about 15 mol % or less (e.g., 14 mol % or less, 13 mol % or less, 12 mol % or less, 11 mol % or less, or about 10.5 mol % or less). The combined amount of Al2O3 and Na2O may be greater than about 5 mol %.
The glass composition of one or more embodiments may exhibit a ratio of the amount of MgO (in mol %) to the total amount of RO (in mol %) in the range from about 0 to about 1. In some embodiments, the ratio MgO/RO is in the range from about 0 to about 0.9, from about 0 to about 0.8, from about 0 to about 0.7, from about 0 to about 0.6, from about 0 to about 0.5, from about 0.1 to about 1, from about 0.2 to about 1, from about 0.3 to about 1, from about 0.4 to about 1, or from about 0.5 to about 1.
In some embodiments, glass composition may be substantially free of nucleating agents. Examples of typical nucleating agents are TiO2, ZrO2 and the like. Nucleating agents may be described in terms of function in that nucleating agents are constituents in the glass can initiate the formation of crystallites in the glass.
In some embodiments, the compositions used for the glass substrate may be batched with from about 0 mol % to about 2 mol % of at least one fining agent selected from any one or more of Na2SO4, NaCl, NaF, NaBr, K2SO4, KCl, KF, KBr, As2O3, Sb2O3, and SnO2. The glass composition according to one or more embodiments may further include SnO2 in the range from about 0 to about 2, from about 0 to about 1, from about 0.1 to about 2, from about 0.1 to about 1, or from about 1 to about 2. The glass compositions disclosed herein may be substantially free of As2O3 and/or Sb2O3.
In one or more embodiments, the composition may specifically include 62 mol % to 75 mol % SiO2; 10.5 mol % to about 17 mol % Al2O3; 5 mol % to about 13 mol % Li2O; 0 mol % to about 4 mol % ZnO; 0 mol % to about 8 mol % MgO; 2 mol % to about 5 mol % TiO2; 0 mol % to about 4 mol % B2O3; 0 mol % to about 5 mol % Na2O; 0 mol % to about 4 mol % K2O; 0 mol % to about 2 mol % ZrO2; 0 mol % to about 7 mol % P2O5; 0 mol % to about 0.3 mol % Fe2O3; 0 mol % to about 2 mol % MnOx; and 0.05 mol % to about 0.2 mol % SnO2.
In one or more embodiments, the composition may include 67 mol % to about 74 mol % SiO2; 11 mol % to about 15 mol % Al2O3; 5.5 mol % to about 9 mol % Li2O; 0.5 mol % to about 2 mol % ZnO; 2 mol % to about 4.5 mol % MgO; 3 mol % to about 4.5 mol % TiO2; 0 mol % to about 2.2 mol % B2O3; 0 mol % to about 1 mol % Na2O; 0 mol % to about 1 mol % K2O; 0 mol % to about 1 mol % ZrO2; 0 mol % to about 4 mol % P2O5; 0 mol % to about 0.1 mol % Fe2O3; 0 mol % to about 1.5 mol % MnOx; and 0.08 mol % to about 0.16 mol % SnO2.
In one or more embodiments, the composition may include 70 mol % to 75 mol % SiO2; 10 mol % to about 15 mol % Al2O3; 5 mol % to about 13 mol % Li2O; 0 mol % to about 4 mol % ZnO; 0.1 mol % to about 8 mol % MgO; 0 mol % to about 5 mol % TiO2; 0.1 mol % to about 4 mol % B2O3; 0.1 mol % to about 5 mol % Na2O; 0 mol % to about 4 mol % K2O; 0 mol % to about 2 mol % ZrO2; 0 mol % to about 7 mol % P2O5; 0 mol % to about 0.3 mol % Fe2O3; 0 mol % to about 2 mol % MnOx; and 0.05 mol % to about 0.2 mol % SnO2.
Other exemplary compositions of glass-based articles prior to being chemically strengthened, as described herein, are shown in Table 1A. Table 1B lists selected physical properties determined for the examples listed in Table 1A. The physical properties listed in Table 1B include: density; low temperature and high temperature CTE; strain, anneal and softening points; 1011 Poise, 35 kP, 200 kP, liquidus, and zircon breakdown temperatures; zircon breakdown and liquidus viscosities; Poisson's ratio; Young's modulus; refractive index, and stress optical coefficient. In some embodiments, the glass-based articles and glass substrates described herein have a high temperature CTE of less than or equal to 30 ppm/° C. and/or a Young's modulus of 70 GPa or more and, in some embodiments, a Young's modulus of up to 80 GPa.
Table 1C shows the properties of Example H after being ion exchanged in a molten salt bath having 80% KNO3 and 20% NaNO3 and a temperature of 430° C. for 16 hours.
Where the glass-based article includes a glass-ceramic, the crystal phases may include β-spodumene, rutile, gahnite or other known crystal phases and combinations thereof.
The glass-based article may be substantially planar, although other embodiments may utilize a curved or otherwise shaped or sculpted substrate. In some instances, the glass-based article may have a 3D or 2.5D shape. The glass-based article may be substantially optically clear, transparent and free from light scattering. The glass-based article may have a refractive index in the range from about 1.45 to about 1.55. As used herein, the refractive index values are with respect to a wavelength of 550 nm.
Additionally or alternatively, the thickness of the glass-based article may be constant along one or more dimension or may vary along one or more of its dimensions for aesthetic and/or functional reasons. For example, the edges of the glass-based article may be thicker as compared to more central regions of the glass-based article. The length, width and thickness dimensions of the glass-based article may also vary according to the article application or use.
The glass-based article may be characterized by the manner in which it is formed. For instance, where the glass-based article may be characterized as float-formable (i.e., formed by a float process), down-drawable and, in particular, fusion-formable or slot-drawable (i.e., formed by a down draw process such as a fusion draw process or a slot draw process).
A float-formable glass-based article may be characterized by smooth surfaces and uniform thickness is made by floating molten glass on a bed of molten metal, typically tin. In an example process, molten glass that is fed onto the surface of the molten tin bed forms a floating glass ribbon. As the glass ribbon flows along the tin bath, the temperature is gradually decreased until the glass ribbon solidifies into a solid glass-based article that can be lifted from the tin onto rollers. Once off the bath, the glass glass-based article can be cooled further and annealed to reduce internal stress. Where the glass-based article is a glass ceramic, the glass-based article formed from the float process may be subjected to a ceramming process by which one or more crystalline phases are generated.
Down-draw processes produce glass-based articles having a uniform thickness that possess relatively pristine surfaces. Because the average flexural strength of the glass-based article is controlled by the amount and size of surface flaws, a pristine surface that has had minimal contact has a higher initial strength. When this high strength glass-based article is then further strengthened (e.g., chemically), the resultant strength can be higher than that of a glass-based article with a surface that has been lapped and polished. Down-drawn glass-based articles may be drawn to a thickness of less than about 2 mm. In addition, down drawn glass-based articles have a very flat, smooth surface that can be used in its final application without costly grinding and polishing. Where the glass-based article is a glass ceramic, the glass-based article formed from the down draw process may be subjected to a ceramming process by which one or more crystalline phases are generated.
The fusion draw process, for example, uses a drawing tank that has a channel for accepting molten glass raw material. The channel has 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 extend down and inwardly so that they join at an edge below the drawing tank. The two flowing glass films join at this edge to fuse and form a single flowing glass-based article. 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 article comes in contact with any part of the apparatus. Thus, the surface properties of the fusion drawn glass-based article are not affected by such contact. Where the glass-based article is a glass ceramic, the glass-based article formed from the fusion process may be subjected to a ceramming process by which one or more crystalline phases are generated.
The slot draw process is distinct from the fusion draw method. In slot draw processes, the molten raw material glass is provided to a drawing tank. The bottom of the drawing tank has an open slot with a nozzle that extends the length of the slot. The molten glass flows through the slot/nozzle and is drawn downward as a continuous glass-based article and into an annealing region. Where the glass-based article is a glass ceramic, the glass-based article formed from the slot draw process may be subjected to a ceramming process by which one or more crystalline phases are generated.
In some embodiments, the glass-based article may be formed using a thin rolling process, as described in U.S. Pat. No. 8,713,972, entitled “Precision Glass Roll Forming Process and Apparatus”, U.S. Pat. No. 9,003,835, entitled “Precision Roll Forming of Textured Sheet Glass”, U.S. Patent Publication No. 20150027169, entitled “Methods And Apparatus For Forming A Glass Ribbon”, and U.S. Patent Publication No. 20050099618, entitled “Apparatus and Method for Forming Thin Glass Articles”, the contents of which are incorporated herein by reference in their entirety. More specifically the glass-based article may be formed by supplying a vertical stream of molten glass, forming the supplied stream of molten glass or glass-ceramic with a pair of forming rolls maintained at a surface temperature of about 500° C. or higher or about 600° C. or higher to form a formed glass ribbon having a formed thickness, sizing the formed ribbon of glass with a pair of sizing rolls maintained at a surface temperature of about 400° C. or lower to produce a sized glass ribbon having a desired thickness less than the formed thickness and a desired thickness uniformity. The apparatus used to form the glass ribbon may include a glass feed device for supplying a supplied stream of molten glass; a pair of forming rolls maintained at a surface temperature of about 500° C. or higher, the forming rolls being spaced closely adjacent each other defining a glass forming gap between the forming rolls with the glass forming gap located vertically below the glass feed device for receiving the supplied stream of molten glass and thinning the supplied stream of molten glass between the forming rolls to form a formed glass ribbon having a formed thickness; and a pair of sizing rolls maintained at a surface temperature of about 400° C. or lower, the sizing rolls being spaced closely adjacent each other defining a glass sizing gap between the sizing rolls with the glass sizing gap located vertically below the forming rolls for receiving the formed glass ribbon and thinning the formed glass ribbon to produce a sized glass ribbon having a desired thickness and a desired thickness uniformity.
In some instances, the thin rolling process may be utilized where the viscosity of the glass does not permit use of fusion or slot draw methods. For example, thin rolling can be utilized to form the glass-based articles when the glass exhibits a liquidus viscosity less than 100 kP.
The glass-based article may be acid polished or otherwise treated to remove or reduce the effect of surface flaws.
Another aspect of this disclosure pertains to devices that include the glass-based articles described herein. For example, the devices may include any device including a display or requiring, strengthened thin glass. In one or more embodiments the devices are electronic devices, which can include mobile devices such as mobile phones, laptops, tablets, mp3 players, navigation devices and the like, or stationary devices such as computers, electronic displays, in vehicle information/entertainment systems, billboards, point of sale systems, navigation systems, and the like). In some embodiments, the glass-based articles described herein may be incorporated into architectural articles (walls, fixtures, panels, windows, etc.), transportation articles (e.g., glazing or interior surfaces in automotive applications, trains, aircraft, sea craft, etc.), appliances (e.g., washers, dryers, dishwashers, refrigerators and the like), or any article that requires some fracture resistance. As shown in
Another aspect of this disclosure pertains to a method of forming a fracture-resistant glass-based article. The method includes providing a glass-based substrate having a first surface and a second surface defining a thickness of about 3 millimeters or less, for example 1 millimeter or less, and generating a stress profile in the glass-based substrate, as described herein to provide the fracture-resistant glass-based article. In one or more embodiments, generating the stress profile comprises ion exchanging a plurality of alkali ions into the glass-based substrate to form a non-zero alkali metal oxide concentration that varies along a substantial portion of the thickness (as described herein) or along the entire thickness. In one example, generating the stress profile includes immersing the glass-based substrate in a molten salt bath including nitrates of Na+, K+, Rb+, Cs+ or a combination thereof, having a temperature of about 350° C. or greater (e.g., about 350° C. to about 500° C.). In one example, the molten bath may include NaNO3, KNO3 or a combination thereof, and may have a temperature of about 485° C. or less. In another example, the bath may include a mixture of NaNO3 and KNO3 and have a temperature of about 460° C. The glass-based substrate may be immersed in the bath for about 2 hours or more, up to about 48 hours (e.g., from about 2 hours to about 10 hours, from about 2 hours to about 8 hours, from about 2 hours to about 6 hours, from about 3 hours to about 10 hours, or from about 3.5 hours to about 10 hours).
In some embodiments, the method may include chemically strengthening or ion exchanging the glass-based substrate in a single bath or in more than one step using successive immersion steps in more than one bath. For example, two or more baths may be used successively. The composition of the one or more baths may include a single metal (e.g., Ag+, Na+, K+, Rb+, or Cs+) or a combination of metals in the same bath. When more than one bath is utilized, the baths may have the same or different composition and/or temperature as one another. The immersion times in each such bath may be the same or may vary to provide the desired stress profile.
In one or more embodiments of the method, a second bath or subsequent baths may be utilized to generate a greater surface CS. In some instances, the method includes immersing the glass-based substrate in the second or subsequent baths to generate a greater surface CS, without significantly influencing the chemical depth of layer and/or the DOC. In such embodiments, the second or subsequent bath may include a single metal (e.g., KNO3 or NaNO3) or a mixture of metals (KNO3 and NaNO3). The temperature of the second or subsequent bath may be tailored to generate the greater surface CS. In some embodiments, the immersion time of the glass-based substrate in the second or subsequent bath may also be tailored to generate a greater surface CS without influencing the chemical depth of layer and/or the DOC. For example, the immersion time in the second or subsequent baths may be less than 10 hours (e.g., about 8 hours or less, about 5 hours or less, about 4 hours or less, about 2 hours or less, about 1 hour or less, about 30 minutes or less, about 15 minutes or less, or about 10 minutes or less).
In one or more alternative embodiments, the method may include one or more heat treatment steps which may be used in combination with the ion-exchanging processes described herein. The heat treatment includes heat treating the glass-based article to obtain a desired stress profile. In some embodiments, heat treating includes annealing, tempering or heating the glass-based substrate to a temperature in the range from about 300° C. to about 600° C. The heat treatment may last for 1 minute up to about 18 hours. In some embodiments, the heat treatment may be used after one or more ion-exchanging processes, or between ion-exchanging processes.
Various embodiments will be further clarified by the following examples. In the Examples, prior to being strengthened, the Examples are referred to as “substrates”. After being subjected to strengthening, the Examples are referred to as “articles” or “glass-based articles”.
Glass-ceramic substrates having a nominal composition as shown below in Table 2 was provided. The glass-ceramic substrates had a thickness of 0.8 millimeters and included a crystal phase assemblage comprising a P-spodumene solid solution as a predominant crystalline phase and one or more minor phases including rutile. The glass-ceramic substrates were immersed in a molten salt bath including NaNO3 having a temperature of 485° C. for 10 hours (Condition A), 13 hours (Condition B) or 24 hours (Condition C), or a molten salt bath including NaNO3 having a temperature of 430° C. for the 2 hours (Comparative Condition D) to form glass-ceramic articles.
The chemical profiles of the glass-ceramic articles were measured by microprobe and are shown in
Sigma(z)=BE/1−n(Cavg−C(z)) (4)
In Equation (4), B is the lattice dilation coefficient, E is Young's modulus, n is Poisson's ratio, and Cavg is in the integral of the concentration across the sample. As shown in
Glass substrates having the same composition as shown in Table 2 and a thickness of 0.8 mm, but having an amorphous structure (and no crystal phases) were chemically strengthened by immersing in a molten salt bath including 100% NaNO3 having a temperature of about 430° C. for various durations to provide glass articles. The DOC and the maximum CT value of the glass articles were measured using a SCALP. As shown in
The stress profiles of the glass articles of Example 2 were measured using SCALP and are shown in
For comparison, the glass-ceramic substrate of Example 1 and the glass substrate of Example 2, each having a thickness of about 0.8 mm, were subjected to chemical strengthening by immersing in a molten salt bath of NaNO3 having a temperature of 350° C. for 3.5 hours (Example 3A and 3B, respectively). The resulting stress profiles (as approximated by the chemical profile measured by microprobe using Equation 4) of the glass-ceramic article and glass article shown in
When the glass-ceramic substrate of Example 1 and the glass substrate of Example 2, each having a thickness of about 0.8 mm were subjected to the chemical strengthening described herein by immersing in a molten salt bath of NaNO3 having a temperature of 430° C. for 24 hours (Examples 3C and 3D, respectively), the resulting glass-based articles exhibited metal oxide concentration profiles (obtained by EPMA) as shown in
Glass substrates (each having a thickness of about 1 mm) having the composition of Table 2 were subjected to chemical strengthening by immersing in a first molten salt bath of NaNO3 having a temperature of 430° C. for 24 hours. One glass-based article was not subjected to any additional strengthening steps (Example 4A). Three glass-based articles were subjected to a second strengthening step by immersion in a second molten salt bath of KNO3 having a temperature of about 430° C. for either 0.75 hours, 4 hours, or 8 hours (Examples 4B, 4C and 4D, respectively). The stress profiles as measured by SCALP of the resulting glass-based articles are shown in
Examples 4E and 4F included glass substrates (each having a thickness of about 1 mm) having the composition of Table 2, which were subjected to chemical strengthening by immersing in a first molten salt bath of NaNO3 having a temperature of 430° C. for 24 hours, followed by heat treatment to a temperature of 430° C. in air for 4 hours or 8.25 hours, respectively. The stress profiles of the glass-based articles of Examples 4E, 4F are shown in
Glass substrates (each having a thickness of about 1 mm) having the composition of Table 2 were subjected to chemical strengthening by immersing in a first molten salt bath of NaNO3 having a temperature of 430° C. for 24 hours. One glass-based article was not subjected to any additional strengthening steps (Example 5A). Two glass-based articles were subjected to a second strengthening step by placing the glass-based articles in a furnace at 390° C. and maintaining the glass-based articles in the furnace for about 8 hours or 28 hours (Examples 5B-5C, respectively). Four glass-based articles were subjected to a third strengthening step (after the first strengthening step and either of the different second strengthening steps) by immersing in a second molten salt bath of KNO3 having a temperature of 430° C. for 4 hours or 8 hours (Examples 5D-5G). The strengthening steps for each of Examples 5A-5G is shown in Table 3. The measured CT values are also shown in Table 3.
The stress profiles of the resulting glass-based articles are shown in
The glass-based articles of Examples 5A-5G were then subjected to a poke test in which one side of the glass-based article is adhered to tape and the opposite bare side is impacted with sharp implement and fractured. The resulting number of fragments can be correlated to the stored tensile energy of the glass-based article. Examples 5A, 5B and 5D exhibited numerous fragments (i.e., in excess of 50 and even 100), while Example 5F exhibited 10 fragments, Example 5C exhibited 3 fragments, and Example 5E and 5G exhibited 4 fragments. Examples 5A, 5B and 5D, which fractured into numerous fragments exhibited higher CT (greater than about 100 MPa) than Examples 5C, 5E, 5F and 5G which all had CT values of about 100 MPa or less.
Glass substrates having a nominal composition as shown in Table 2 and each having a thickness of about 1 mm were subjected to chemical strengthening in a molten salt bath including 100% NaNO3 and a temperature of 430° C. The duration for which the glass substrates were immersed in the molten salt bath are shown in Table 5.
The stress profiles of the glass-based articles of Examples 6A-6G are shown in
Glass substrates having a nominal composition as shown in Table 2 and having a thicknesses of about 0.8 mm each were subjected to chemical strengthening in a molten salt bath including a mixture of NaNO3 and NaSO4 and a temperature of 500° C. for 15 minutes (Comparative Example 7A) and for 16 hours (Example 7B). The stress profile of the glass-based articles of Examples 7A and 7B are shown in
As shown in
Glass substrates having a nominal composition as shown in Table 2 and having a thicknesses of about 1 mm each were subjected to chemical strengthening in a molten salt bath including NaNO3 and a temperature of 430° C. for 4 hours (Comparative Example 7C) and for 61.5 hours (Example 7D). Comparative Example 7C exhibited a known stress profile, whereas, Example 7D showed a stress profile according to one or more embodiments of this disclosure. The stored tensile energy of Examples 7C and 7D was calculated using the same method used with Examples 4B-4D and plotted as a function of measured CT (MPa), as shown in
As shown in
Glass substrates having a nominal composition of 70.9 mol % SiO2, 12.8 mol % Al2O3, 1.95 mol % B2O3, 7.95 mol % Li2O, 2.43 mol % Na2O, 2.98 mol % MgO, 0.89 mol % ZnO, and 0.1 mol % SnO2 and having a thicknesses of about 0.8 mm were subjected the ion exchange conditions of Table 5. Various properties of Example 8 are compared to Example 2 in Table 6.
The stress profiles of the glass-based articles of Example 8 were measured and exhibited the shapes described herein.
Glass substrates according to Example 2, Comparative Examples 8A and 8B were provided having the same thickness as Example 8. The glass substrates according to Example 2 were ion exchanged in a molten bath of 100% NaNO3, having a temperature of 430° C. for 33 hours. Comparative Example 8A was ion exchanged in a molten bath of 100% NaNO3, having a temperature of 390° C. for 16 hours and also exhibited a known error function stress profile. The glass substrates according to Example 8B included a nominal composition of 57.5 mol % SiO2, 16.5 mol % Al2O3, 16.7 mol % Na2O, 2.5 mol % MgO, and 6.5 mol % P2O5 and were ion exchanged to exhibit a known error function stress profile. As used herein, the term “error function stress profile” refers to a stress profile resembling
The glass-based articles from Example 2, Example 8 and Comparative Examples 8A and 8B were then retrofitted onto identical mobile phone devices. The phone devices were dropped from incremental heights starting at 20 centimeters onto 30 grit sandpaper. If a glass-based article survived the drop from one height (e.g., 20 cm), the mobile phone was dropped again from a greater height (e.g., 30 cm, 40 cm, 50 cm, etc.). The height at which the glass-based article failed is plotted in
The same test was repeated with new samples using the same mobile phone device onto 180 grit sandpaper. The average failure height for Comparative Example 8A was 204 cm, the average failure height for Comparative Example 8B was 190 cm, the average failure height for Example 2 was 214 cm and the average failure height for Example 8 was 214 cm.
Glass substrates according to Comparative Example 8C, having a nominal composition of 65 mol % SiO2, 5 mol % B2O3, 14 mol % Al2O3, 14 mol % Na2O, 2 mol % MgO, and 0.1 mol % SnO2 and a thickness of 0.8 mm, were ion exchanged to exhibit a known error function stress profile The glass-based article samples of Example 2 and Comparative Example 8B (exhibiting the stress profile described above in this Example), Comparative Example 8C and the glass-based articles of Example 8 ion exchanged according to Condition 4, as shown in Table 5, were subjected to A-ROR testing as described herein.
Examples 6 and 8 and Comparative Example 8C were abraded using a load or pressure of 25 psi and 45 psi, and Example 2 was abraded using a load of 25 psi, only. The AROR data is shown in
Glass-based article samples of Examples 2 (ion exchanged as described above in this Example) and 8 (ion exchanged according to Condition 4) were subjected a 4-point bend test. The results are shown in the Weibull distribution plot of
As shown above, glass-based articles made from compositions having a strain point greater than 525° C. enable ion exchange temperatures (or ion exchange bath temperatures) in the range from about 350° C. to about 480° C. In some embodiments, glass compositions exhibiting a monovalent ion diffusivity greater than about 800 square micrometers/hour enable the metal oxides diffusing into the glass-based article to penetrate the entire depth or thickness of the article quickly such that stress relaxation is minimized. Excessive stress relaxation can reduce the surface compressive stress of the glass-based article.
It will be apparent to those skilled in the art that various modifications and variations can be made without departing from the spirit or scope of the invention.
Glass substrates having the same composition as Example 8 and a thickness of about 0.8 mm, were subjected the ion exchange by immersing in a 100% NaNO3 molten salt bath having a temperature of 430° C. according to the conditions provided in Table 7. The resulting glass-based articles exhibited maximum CT values, which are plotted as a function of ion exchange time in
The stress profile for Example 9D was measured using a refracted near-field (RNF) measurement, as described in U.S. Pat. No. 8,854,623, entitled “Systems and methods for measuring a profile characteristic of a glass sample”, which is incorporated herein by reference in its entirety.
Example 10A included a glass substrate having the same composition as Example 1 and a thickness of 0.8 mm. The glass substrate was ion exchanged in a single molten salt bath including 80% KNO3 and 20% NaNO3, and having a temperature of about 430° C., for 16 hours. The resulting glass-based article exhibited the stress profile as described in Table 9.
Glass-based articles according to Example 10A were subjected to AROR testing as described herein. One set of glass-based articles was abraded using a load or pressure of 5 psi, a second set of glass-based articles was abraded using a load or pressure of 25 psi, and a third set of glass-based articles was abraded using a load or pressure of 45 psi. The AROR data is shown in
Glass-based articles according to Example 10A were retrofitted onto identical mobile phone devices. The phone devices were dropped from incremental heights starting at 20 centimeters onto 180 grit sandpaper. If a glass-based article survived the drop from one height (e.g., 20 cm), the mobile phone was dropped again from a greater height (e.g., 30 cm, 40 cm, 50 cm, etc.) up to a height of 225 cm. The surviving glass-based articles were then dropped onto 30 grit sandpaper (in the same phone devices). The height at which the glass-based article failed on both 180 grit sandpaper and 30 grit sandpaper is plotted in
The glass-based articles according to Example 10A exhibited a dielectric constant of about 5.8 to about 6 over a frequency range from about 480 mHz to about 3000 mHz. The glass-based articles according to Example 10A exhibited a dielectric loss tangent in the range from about 0.010 to about 0.013 over a frequency range from about 480 mHz to about 3000 mHz.
The refractive index of the glass-based articles according to Example 10A is in the range from about 1.496 to about 1.523 over a range from about 380 nm to about 1550 nm, and from about 1.496 to about 1.503 over a wavelength range from about 380 nm to about 800 nm.
The glass-based articles according to Example 10A were subjected to various chemical treatments as shown in Table 10. The chemical durability of the glass-based articles was compared to Comparative Examples 10B, 10C and 10D. Comparative Example 10B was a glass substrate having a nominal composition of 64.3 mol % SiO2, 7.02 mol % B2O3, 14 mol % Al2O3, 14 mol % Na2O, 0.5 mol % K2O, 0.03 mol % Fe2O3, and 0.1 mol % SnO2. Comparative Example 10C was a glass substrate having a nominal composition of 64.75 mol % SiO2, 5 mol % B2O3, 14 mol % Al2O3, 13.75 mol % Na2O, 2.4 mol % MgO, and 0.08 mol % SnO2. Comparative Example 10D included a glass substrate having a nominal composition of 57.5 mol % SiO2, 16.5 mol % Al2O3, 16.71 mol % Na2O, 2.8 mol % MgO, 0.05 mol % SnO2 and 6.5 mol % P2O5.
Example 11A included glass substrates having the same composition as Example 1 and a thickness of 0.8 mm. Comparative Example 11B included glass substrates having the same composition as Comparative Example 10D and a thickness of 0.8 mm. The glass substrates of Example 11A were chemically strengthened in a single step using a single bath, as described in Table 11. The glass substrates of Comparative Example 3B was ion exchanged in a two-step process, as described in Table 11.
The glass-based articles according to Example 11A and Comparative Example 11B were retrofitted onto identical mobile phone devices. The phone devices were dropped from incremental heights starting at 20 centimeters onto 30 grit sandpaper. The height at which the glass-based article failed on 30 grit sandpaper is plotted in
Glass-based articles according to Example 11A and Comparative Example 11B were subjected to AROR testing, as described herein, using a load or pressure of 25 psi. The glass-based substrates of Example 10A exhibited an average load to failure of about 31.3 kgf, while the glass-based substrates of Comparative Example 10B exhibited an average load to failure of about 27.4 kgf, as shown in
Examples 12A and 12B included glass substrates having the nominal composition as in Example 1H and a thickness of 0.8 mm. The glass substrates of Examples 12A were chemically strengthened at 430° C. in a bath having 6.5% Na:93.5% K for 4.5 hours, and resulted in a CS of about 656, a DOL of about 8.1, and a CSk (or compressive stress at the knee) of from about 105 to about 130 MPa. The substrates of Examples 12B were chemically strengthened at a temperature of 430° C. in a bath having 70% Na:93% K for 4.5 hours, and resulted in a CS of about 640 MPa, a DOL of about 8.2, and a CSk of about 100 MPa. Examples 12A and 12B were subjected to inverted ball drop on sandpaper (IBoS) tests according to the procedure described herein. The tests were conducted using 30 grit sandpaper and a 4.2 g stainless steel ball having a diameter of 10 mm.
Sample set 12A exhibited an average fracture height of 88 cm. Additionally, four out of five samples withstood drop heights of each 75 cm, 80 cm, 85 cm, 90 cm, and 95 cm, leading to an 80% survival rate at each of these heights. Sample set 12B exhibited an average fracture height of 76 cm. Additionally, three out of five samples withstood drop heights of each 75 cm, 80 cm, and 85 cm, leading to a 60% survival rate at each of these heights.
Sample sets 12A and 12B were also subject to Knoop Scratch Threshold testing as described above. The Samples of set 12A had a Knoop Scratch Threshold of greater than 7 N and less than 14 N. On the other hand, the Samples of set 12B had a Knoop Scratch Threshold of greater than 10 N and less than 16 N.
It will be apparent to those skilled in the art that various modifications and variations can be made without departing from the spirit or scope of the invention. For example, the various features can be combined according to the following exemplary embodiments.
This application is a divisional application and claims the benefit of priority under 35 U.S.C. § 120 of U.S. application Ser. No. 17/695,948 filed on Mar. 16, 2022, which is a divisional application and claims the benefit of priority under 35 U.S.C. § 120 of U.S. Pat. No. 11,279,652 granted on Mar. 22, 2022, which is a divisional and claims the benefit of priority under 35 U.S.C. § 120 of U.S. patent Ser. No. 10/570,059 granted on Feb. 25, 2020, which is a divisional application and claims the benefit of priority under 35 U.S.C. § 120 of U.S. patent Ser. No. 10/017,417 granted on Jul. 10, 2018, which in turn, claims the benefit of priority under 35 U.S.C. § 119 of U.S. Provisional Application Ser. No. 62/366,338 filed on Jul. 25, 2016 and U.S. Provisional Application Ser. No. 62/320,077 filed on Apr. 8, 2016, the contents of each of which are relied upon and incorporated herein by reference in their entireties.
| Number | Name | Date | Kind |
|---|---|---|---|
| 1960121 | Moulton | May 1934 | A |
| 3107196 | Acloque | Oct 1963 | A |
| 3287200 | Hess et al. | Nov 1966 | A |
| 3357876 | Rinehart | Dec 1967 | A |
| 3380818 | Smith | Apr 1968 | A |
| 3404015 | Dumbaugh, Jr. | Oct 1968 | A |
| 3410673 | Marusak | Nov 1968 | A |
| 3433611 | Saunders et al. | Mar 1969 | A |
| 3464880 | Rinehart | Sep 1969 | A |
| 3489097 | William | Jan 1970 | A |
| 3490984 | Petticrew et al. | Jan 1970 | A |
| 3597305 | Giffen | Aug 1971 | A |
| 3625718 | Petticrew | Dec 1971 | A |
| 3639198 | Plumat et al. | Feb 1972 | A |
| 3656923 | Garfinkel et al. | Apr 1972 | A |
| 3660060 | Spanoudis | May 1972 | A |
| 3673049 | Giffen et al. | Jun 1972 | A |
| 3737294 | Dumbaugh et al. | Jun 1973 | A |
| 3746526 | Giffon | Jul 1973 | A |
| 3765855 | Larrick | Oct 1973 | A |
| 3798013 | Hasegawa et al. | Mar 1974 | A |
| 3811855 | Stockdale et al. | May 1974 | A |
| 3833388 | Ohlberg et al. | Sep 1974 | A |
| 3844754 | Grubb et al. | Oct 1974 | A |
| 3879183 | Carlson | Apr 1975 | A |
| 3907577 | Kiefer et al. | Sep 1975 | A |
| 3931438 | Beall et al. | Jan 1976 | A |
| 3936287 | Beall et al. | Feb 1976 | A |
| 3958052 | Galusha et al. | May 1976 | A |
| 3959000 | Nakagawa et al. | May 1976 | A |
| 4042405 | Krohn et al. | Aug 1977 | A |
| 4053679 | Rinehart | Oct 1977 | A |
| 4055703 | Rinehart | Oct 1977 | A |
| 4102664 | Dumbaugh, Jr. | Jul 1978 | A |
| 4130437 | Mazeau et al. | Dec 1978 | A |
| 4148661 | Kerko et al. | Apr 1979 | A |
| 4156755 | Rinehart | May 1979 | A |
| 4190451 | Hares et al. | Feb 1980 | A |
| 4192688 | Babcock | Mar 1980 | A |
| 4214886 | Shay et al. | Jul 1980 | A |
| 4240836 | Borrelli et al. | Dec 1980 | A |
| 4242117 | van Ass | Dec 1980 | A |
| 4358542 | Hares et al. | Nov 1982 | A |
| 4407966 | Kerko et al. | Oct 1983 | A |
| 4468534 | Boddicker | Aug 1984 | A |
| 4471024 | Pargamin et al. | Sep 1984 | A |
| 4483700 | Forker et al. | Nov 1984 | A |
| 4537612 | Borrelli et al. | Aug 1985 | A |
| 4608349 | Kerko et al. | Aug 1986 | A |
| 4702042 | Herrington et al. | Oct 1987 | A |
| 4726981 | Pierson et al. | Feb 1988 | A |
| 4736981 | Barton et al. | Apr 1988 | A |
| 4757162 | Dumora et al. | Jul 1988 | A |
| 4857485 | Brennan et al. | Aug 1989 | A |
| 5270269 | Hares et al. | Dec 1993 | A |
| 5273827 | Francis | Dec 1993 | A |
| 5322819 | Araujo et al. | Jun 1994 | A |
| 5342426 | Dumbaugh, Jr. | Aug 1994 | A |
| 5350607 | Tyson et al. | Sep 1994 | A |
| 5559060 | Dumbaugh et al. | Sep 1996 | A |
| 5763343 | Brix et al. | Jun 1998 | A |
| 5773148 | Charrue et al. | Jun 1998 | A |
| 5804317 | Charrue | Sep 1998 | A |
| 5895768 | Speit | Apr 1999 | A |
| 5972460 | Tachiwana | Oct 1999 | A |
| 6111821 | Bach | Aug 2000 | A |
| 6187441 | Takeuchi et al. | Feb 2001 | B1 |
| 6333286 | Kurachi et al. | Dec 2001 | B1 |
| 6376402 | Pannhorst et al. | Apr 2002 | B1 |
| 6413892 | Koyama et al. | Jul 2002 | B1 |
| 6440531 | Kurachi et al. | Aug 2002 | B1 |
| 6472068 | Glass et al. | Oct 2002 | B1 |
| 6514149 | Yoon | Feb 2003 | B2 |
| 6516634 | Green et al. | Feb 2003 | B1 |
| 6518211 | Bradshaw et al. | Feb 2003 | B1 |
| 6528440 | Vilato et al. | Mar 2003 | B1 |
| 6537938 | Miyazaki | Mar 2003 | B1 |
| 6607999 | Hachitani | Aug 2003 | B2 |
| 6689704 | Ota et al. | Feb 2004 | B2 |
| 6846760 | Siebers et al. | Jan 2005 | B2 |
| 7007512 | Kamada et al. | Mar 2006 | B2 |
| 7091141 | Horsfall et al. | Aug 2006 | B2 |
| 7176528 | Couillard et al. | Feb 2007 | B2 |
| 7476633 | Comte et al. | Jan 2009 | B2 |
| 7514149 | Bocko et al. | Apr 2009 | B2 |
| 7531475 | Kishimoto et al. | May 2009 | B2 |
| 7619283 | Gadkaree | Nov 2009 | B2 |
| 7666511 | Ellison et al. | Feb 2010 | B2 |
| 7687419 | Kawai | Mar 2010 | B2 |
| 7727917 | Shelestak et al. | Jun 2010 | B2 |
| 7838136 | Nakashima et al. | Nov 2010 | B2 |
| 7891212 | Isono | Feb 2011 | B2 |
| 8007913 | Coppola et al. | Aug 2011 | B2 |
| 8075999 | Barefoot et al. | Dec 2011 | B2 |
| 8099982 | Takagi et al. | Jan 2012 | B2 |
| 8143179 | Aitken et al. | Mar 2012 | B2 |
| 8158543 | Dejneka et al. | Apr 2012 | B2 |
| 8193128 | Hellmann et al. | Jun 2012 | B2 |
| 8232218 | Dejneka et al. | Jul 2012 | B2 |
| 8252708 | Morena et al. | Aug 2012 | B2 |
| 8312739 | Lee et al. | Nov 2012 | B2 |
| 8312789 | Beck | Nov 2012 | B2 |
| 8327666 | Harvey et al. | Dec 2012 | B2 |
| 8347651 | Abramov et al. | Jan 2013 | B2 |
| 8349455 | Kondo et al. | Jan 2013 | B2 |
| 8415013 | Barefoot et al. | Apr 2013 | B2 |
| 8431502 | Dejneka et al. | Apr 2013 | B2 |
| 8561429 | Allan et al. | Oct 2013 | B2 |
| 8580411 | Endo et al. | Nov 2013 | B2 |
| 8586492 | Barefoot et al. | Nov 2013 | B2 |
| 8623776 | Dejneka et al. | Jan 2014 | B2 |
| 8652978 | Dejneka et al. | Feb 2014 | B2 |
| 8656734 | Zou et al. | Feb 2014 | B2 |
| 8691711 | Nakashima et al. | Apr 2014 | B2 |
| 8697592 | Ikenishi et al. | Apr 2014 | B2 |
| 8713972 | Lakota et al. | May 2014 | B2 |
| 8756262 | Zhang | Jun 2014 | B2 |
| 8759238 | Chapman et al. | Jun 2014 | B2 |
| 8765262 | Gross | Jul 2014 | B2 |
| 8778820 | Gomez et al. | Jul 2014 | B2 |
| 8783063 | Osakabe et al. | Jul 2014 | B2 |
| 8802581 | Dejneka et al. | Aug 2014 | B2 |
| 8854623 | Fontaine et al. | Oct 2014 | B2 |
| 8932510 | Li et al. | Jan 2015 | B2 |
| 8943855 | Gomez et al. | Feb 2015 | B2 |
| 8946103 | Dejneka et al. | Feb 2015 | B2 |
| 8950215 | Rappoport et al. | Feb 2015 | B2 |
| 8951927 | Dejneka et al. | Feb 2015 | B2 |
| 8957374 | Liu et al. | Feb 2015 | B2 |
| 8969226 | Dejneka et al. | Mar 2015 | B2 |
| 8975374 | Kimura | Mar 2015 | B2 |
| 9003835 | Lock | Apr 2015 | B2 |
| 9007878 | Matsumoto et al. | Apr 2015 | B2 |
| 9139469 | Comte et al. | Sep 2015 | B2 |
| 9140543 | Allan et al. | Sep 2015 | B1 |
| 9145329 | Drake et al. | Sep 2015 | B2 |
| 9156724 | Gross | Oct 2015 | B2 |
| 9193625 | Bookbinder et al. | Nov 2015 | B2 |
| 9212288 | Fujiwara et al. | Dec 2015 | B2 |
| 9272945 | Smith | Mar 2016 | B2 |
| 9290407 | Barefoot et al. | Mar 2016 | B2 |
| 9290413 | Dejneka et al. | Mar 2016 | B2 |
| 9339993 | Cites et al. | May 2016 | B2 |
| 9346703 | Bookbinder et al. | May 2016 | B2 |
| 9359251 | Bookbinder et al. | Jun 2016 | B2 |
| 9487434 | Amin et al. | Nov 2016 | B2 |
| 9498822 | Brandt et al. | Nov 2016 | B2 |
| 9499431 | Barefoot et al. | Nov 2016 | B2 |
| 9567254 | Amin et al. | Feb 2017 | B2 |
| 9593042 | Hu et al. | Mar 2017 | B2 |
| 9604876 | Gy et al. | Mar 2017 | B2 |
| 9676663 | Amin et al. | Jun 2017 | B2 |
| 9701569 | Demartino et al. | Jul 2017 | B2 |
| 9751802 | Allan et al. | Sep 2017 | B2 |
| 9840435 | Ohara et al. | Dec 2017 | B2 |
| 9902648 | Amin et al. | Feb 2018 | B2 |
| 9908810 | Amin et al. | Mar 2018 | B2 |
| 9908811 | Gross et al. | Mar 2018 | B2 |
| 9977470 | Demartino et al. | May 2018 | B2 |
| 10017417 | Dejneka | Jul 2018 | B2 |
| 10118858 | Amin et al. | Nov 2018 | B2 |
| 10144670 | Akatsuka et al. | Dec 2018 | B2 |
| 10150698 | Amin et al. | Dec 2018 | B2 |
| 10160688 | Amin et al. | Dec 2018 | B2 |
| 10239784 | Oram et al. | Mar 2019 | B2 |
| 10259746 | Hu et al. | Apr 2019 | B2 |
| 10570059 | Dejneka | Feb 2020 | B2 |
| 10579106 | Demartino et al. | Mar 2020 | B2 |
| 10787387 | Gross et al. | Sep 2020 | B2 |
| 11174197 | Dejneka | Nov 2021 | B2 |
| 11279652 | Dejneka | Mar 2022 | B2 |
| 11691913 | Dejneka | Jul 2023 | B2 |
| 20020023463 | Siebers et al. | Feb 2002 | A1 |
| 20050090377 | Shelestak et al. | Apr 2005 | A1 |
| 20050099618 | Difoggio et al. | May 2005 | A1 |
| 20050143247 | Siebers et al. | Jun 2005 | A1 |
| 20050215414 | Kawai | Sep 2005 | A1 |
| 20050221044 | Gaume et al. | Oct 2005 | A1 |
| 20050250639 | Siebers et al. | Nov 2005 | A1 |
| 20060127679 | Gulati et al. | Jun 2006 | A1 |
| 20060279217 | Peuchert et al. | Dec 2006 | A1 |
| 20070060465 | Varshneya et al. | Mar 2007 | A1 |
| 20070122580 | Krall et al. | May 2007 | A1 |
| 20070123410 | Morena et al. | May 2007 | A1 |
| 20070218262 | Degand et al. | Sep 2007 | A1 |
| 20080026927 | Monique Comte | Jan 2008 | A1 |
| 20080128953 | Nagai et al. | Jun 2008 | A1 |
| 20080241603 | Isono | Oct 2008 | A1 |
| 20080286548 | Ellison et al. | Nov 2008 | A1 |
| 20090142568 | Dejneka et al. | Jun 2009 | A1 |
| 20090197088 | Murata | Aug 2009 | A1 |
| 20090215607 | Dejneka et al. | Aug 2009 | A1 |
| 20090220761 | Dejneka et al. | Sep 2009 | A1 |
| 20090286091 | Danielson et al. | Nov 2009 | A1 |
| 20100003508 | Arrouy et al. | Jan 2010 | A1 |
| 20100009154 | Allan et al. | Jan 2010 | A1 |
| 20100028607 | Lee et al. | Feb 2010 | A1 |
| 20100029460 | Shojiya et al. | Feb 2010 | A1 |
| 20100035038 | Barefoot et al. | Feb 2010 | A1 |
| 20100035745 | Murata | Feb 2010 | A1 |
| 20100087307 | Murata et al. | Apr 2010 | A1 |
| 20100112341 | Takagi et al. | May 2010 | A1 |
| 20100119846 | Sawada | May 2010 | A1 |
| 20100190038 | Osakabe et al. | Jul 2010 | A1 |
| 20100200804 | Woodruff et al. | Aug 2010 | A1 |
| 20100210422 | Crawford | Aug 2010 | A1 |
| 20100210442 | Abramov et al. | Aug 2010 | A1 |
| 20100215996 | Wendling et al. | Aug 2010 | A1 |
| 20100291353 | Dejneka et al. | Nov 2010 | A1 |
| 20100326657 | Hellmann et al. | Dec 2010 | A1 |
| 20110014475 | Murata | Jan 2011 | A1 |
| 20110064951 | Fujiwara et al. | Mar 2011 | A1 |
| 20110067447 | Zadesky et al. | Mar 2011 | A1 |
| 20110092353 | Amin et al. | Apr 2011 | A1 |
| 20110165393 | Bayne et al. | Jul 2011 | A1 |
| 20110201490 | Barefoot et al. | Aug 2011 | A1 |
| 20110226832 | Bayne et al. | Sep 2011 | A1 |
| 20110281093 | Gulati et al. | Nov 2011 | A1 |
| 20110293942 | Cornejo et al. | Dec 2011 | A1 |
| 20110294648 | Chapman et al. | Dec 2011 | A1 |
| 20110294649 | Gomez et al. | Dec 2011 | A1 |
| 20110312483 | Nakashima et al. | Dec 2011 | A1 |
| 20120015150 | Suzuki | Jan 2012 | A1 |
| 20120021898 | Elam et al. | Jan 2012 | A1 |
| 20120040146 | Garner et al. | Feb 2012 | A1 |
| 20120048604 | Cornejo et al. | Mar 2012 | A1 |
| 20120052271 | Gomez et al. | Mar 2012 | A1 |
| 20120052275 | Hashimoto et al. | Mar 2012 | A1 |
| 20120083401 | Koyama et al. | Apr 2012 | A1 |
| 20120114955 | Almoric et al. | May 2012 | A1 |
| 20120135153 | Osakabe et al. | May 2012 | A1 |
| 20120135226 | Bookbinder et al. | May 2012 | A1 |
| 20120135848 | Beall et al. | May 2012 | A1 |
| 20120171497 | Koyama et al. | Jul 2012 | A1 |
| 20120174497 | Kroes | Jul 2012 | A1 |
| 20120189843 | Chang et al. | Jul 2012 | A1 |
| 20120194974 | Weber et al. | Aug 2012 | A1 |
| 20120196110 | Murata et al. | Aug 2012 | A1 |
| 20120206406 | Kim et al. | Aug 2012 | A1 |
| 20120216565 | Allan et al. | Aug 2012 | A1 |
| 20120216569 | Allan et al. | Aug 2012 | A1 |
| 20120219792 | Yamamoto et al. | Aug 2012 | A1 |
| 20120235953 | Kim et al. | Sep 2012 | A1 |
| 20120236526 | Weber | Sep 2012 | A1 |
| 20120264585 | Ohara et al. | Oct 2012 | A1 |
| 20120297829 | Endo et al. | Nov 2012 | A1 |
| 20120308827 | Boek et al. | Dec 2012 | A1 |
| 20120321898 | Meinhardt et al. | Dec 2012 | A1 |
| 20130004758 | Dejneka et al. | Jan 2013 | A1 |
| 20130007458 | Wakita et al. | Jan 2013 | A1 |
| 20130017380 | Murata et al. | Jan 2013 | A1 |
| 20130045375 | Gross | Feb 2013 | A1 |
| 20130050992 | Schneider et al. | Feb 2013 | A1 |
| 20130101596 | Demartino et al. | Apr 2013 | A1 |
| 20130101798 | Hashimoto | Apr 2013 | A1 |
| 20130122260 | Liang | May 2013 | A1 |
| 20130122284 | Gross | May 2013 | A1 |
| 20130183512 | Gy et al. | Jul 2013 | A1 |
| 20130186139 | Tanii | Jul 2013 | A1 |
| 20130189486 | Wang et al. | Jul 2013 | A1 |
| 20130202868 | Barefoot et al. | Aug 2013 | A1 |
| 20130203583 | Zhang et al. | Aug 2013 | A1 |
| 20130209751 | Zhang et al. | Aug 2013 | A1 |
| 20130219966 | Hasegawa et al. | Aug 2013 | A1 |
| 20130224492 | Bookbinder et al. | Aug 2013 | A1 |
| 20130236666 | Bookbinder et al. | Sep 2013 | A1 |
| 20130236699 | Prest et al. | Sep 2013 | A1 |
| 20130240025 | Bersano et al. | Sep 2013 | A1 |
| 20130260154 | Allan et al. | Oct 2013 | A1 |
| 20130274085 | Beall et al. | Oct 2013 | A1 |
| 20130288001 | Murata et al. | Oct 2013 | A1 |
| 20130288010 | Akarapu et al. | Oct 2013 | A1 |
| 20130309613 | O'Malley et al. | Nov 2013 | A1 |
| 20130323444 | Ehemann et al. | Dec 2013 | A1 |
| 20140023865 | Comte et al. | Jan 2014 | A1 |
| 20140050911 | Mauro et al. | Feb 2014 | A1 |
| 20140063393 | Zhong et al. | Mar 2014 | A1 |
| 20140066284 | Hashimoto et al. | Mar 2014 | A1 |
| 20140087159 | Cleary et al. | Mar 2014 | A1 |
| 20140087193 | Cites et al. | Mar 2014 | A1 |
| 20140087194 | Dejneka et al. | Mar 2014 | A1 |
| 20140090864 | Paulson | Apr 2014 | A1 |
| 20140092377 | Liu et al. | Apr 2014 | A1 |
| 20140093702 | Kitajima | Apr 2014 | A1 |
| 20140106141 | Bellman et al. | Apr 2014 | A1 |
| 20140106172 | Dejneka et al. | Apr 2014 | A1 |
| 20140109616 | Varshneya | Apr 2014 | A1 |
| 20140113141 | Yamamoto et al. | Apr 2014 | A1 |
| 20140134397 | Amin et al. | May 2014 | A1 |
| 20140139978 | Kwong | May 2014 | A1 |
| 20140141226 | Bookbinder et al. | May 2014 | A1 |
| 20140147576 | Lewis et al. | May 2014 | A1 |
| 20140150525 | Okawa et al. | Jun 2014 | A1 |
| 20140151370 | Chang et al. | Jun 2014 | A1 |
| 20140154661 | Bookbinder et al. | Jun 2014 | A1 |
| 20140170380 | Murata et al. | Jun 2014 | A1 |
| 20140193606 | Kwong | Jul 2014 | A1 |
| 20140220327 | Adib et al. | Aug 2014 | A1 |
| 20140227523 | Dejneka et al. | Aug 2014 | A1 |
| 20140227524 | Ellison et al. | Aug 2014 | A1 |
| 20140227525 | Matsuda et al. | Aug 2014 | A1 |
| 20140234607 | Matsuda et al. | Aug 2014 | A1 |
| 20140248495 | Matsuda et al. | Sep 2014 | A1 |
| 20140308526 | Chapman et al. | Oct 2014 | A1 |
| 20140321124 | Schneider et al. | Oct 2014 | A1 |
| 20140329660 | Barefoot et al. | Nov 2014 | A1 |
| 20140335330 | Bellman et al. | Nov 2014 | A1 |
| 20140356576 | Dejneka et al. | Dec 2014 | A1 |
| 20140356605 | Adib et al. | Dec 2014 | A1 |
| 20140364298 | Ohara et al. | Dec 2014 | A1 |
| 20140370264 | Ohara et al. | Dec 2014 | A1 |
| 20140370302 | Amin et al. | Dec 2014 | A1 |
| 20150004390 | Kawamoto et al. | Jan 2015 | A1 |
| 20150011811 | Pavone et al. | Jan 2015 | A1 |
| 20150027169 | Fredholm | Jan 2015 | A1 |
| 20150030834 | Morey et al. | Jan 2015 | A1 |
| 20150030838 | Sellier et al. | Jan 2015 | A1 |
| 20150037543 | Keegan et al. | Feb 2015 | A1 |
| 20150037586 | Gross | Feb 2015 | A1 |
| 20150044473 | Murata et al. | Feb 2015 | A1 |
| 20150052949 | Bayne et al. | Feb 2015 | A1 |
| 20150060401 | Chang et al. | Mar 2015 | A1 |
| 20150064472 | Gross et al. | Mar 2015 | A1 |
| 20150064474 | Dejneka et al. | Mar 2015 | A1 |
| 20150074974 | Pesansky et al. | Mar 2015 | A1 |
| 20150079398 | Amin et al. | Mar 2015 | A1 |
| 20150083200 | Hickman et al. | Mar 2015 | A1 |
| 20150093581 | Murata et al. | Apr 2015 | A1 |
| 20150111030 | Miyasaka et al. | Apr 2015 | A1 |
| 20150132563 | O'Malley et al. | May 2015 | A1 |
| 20150140325 | Gross et al. | May 2015 | A1 |
| 20150144291 | Brandt et al. | May 2015 | A1 |
| 20150147574 | Allan et al. | May 2015 | A1 |
| 20150147575 | Dejneka et al. | May 2015 | A1 |
| 20150147576 | Bookbinder et al. | May 2015 | A1 |
| 20150152003 | Kawamoto et al. | Jun 2015 | A1 |
| 20150157533 | Demartino et al. | Jun 2015 | A1 |
| 20150166401 | Yamamoto | Jun 2015 | A1 |
| 20150166407 | Varshneya et al. | Jun 2015 | A1 |
| 20150175469 | Tabe | Jun 2015 | A1 |
| 20150183680 | Barefoot et al. | Jul 2015 | A1 |
| 20150239775 | Amin et al. | Aug 2015 | A1 |
| 20150239776 | Amin et al. | Aug 2015 | A1 |
| 20150251947 | Lestrigant et al. | Sep 2015 | A1 |
| 20150259244 | Amin et al. | Sep 2015 | A1 |
| 20150261363 | Shah et al. | Sep 2015 | A1 |
| 20150274585 | Rogers et al. | Oct 2015 | A1 |
| 20150329413 | Beall et al. | Nov 2015 | A1 |
| 20150329418 | Murata et al. | Nov 2015 | A1 |
| 20150368148 | Duffy et al. | Dec 2015 | A1 |
| 20150368153 | Pesansky et al. | Dec 2015 | A1 |
| 20160083291 | Dogimont et al. | Mar 2016 | A1 |
| 20160102011 | Hu et al. | Apr 2016 | A1 |
| 20160102014 | Hu et al. | Apr 2016 | A1 |
| 20160107924 | Yamamoto et al. | Apr 2016 | A1 |
| 20160122239 | Amin et al. | May 2016 | A1 |
| 20160122240 | Oram et al. | May 2016 | A1 |
| 20160187994 | La et al. | Jun 2016 | A1 |
| 20160265368 | Bencini et al. | Sep 2016 | A1 |
| 20160318796 | Masuda | Nov 2016 | A1 |
| 20160333776 | Andersson et al. | Nov 2016 | A1 |
| 20170022092 | Demartino et al. | Jan 2017 | A1 |
| 20170022093 | Demartino et al. | Jan 2017 | A1 |
| 20170158556 | Dejneka et al. | Jun 2017 | A1 |
| 20170166478 | Gross et al. | Jun 2017 | A1 |
| 20170197869 | Beall et al. | Jul 2017 | A1 |
| 20170197870 | Finkeldey et al. | Jul 2017 | A1 |
| 20170291849 | Dejneka et al. | Oct 2017 | A1 |
| 20170295657 | Gross et al. | Oct 2017 | A1 |
| 20170305786 | Roussev et al. | Oct 2017 | A1 |
| 20190208652 | Gross et al. | Jul 2019 | A1 |
| Number | Date | Country |
|---|---|---|
| 6452265 | Oct 1965 | AU |
| 2011212982 | Aug 2012 | AU |
| 1312582 | Sep 2001 | CN |
| 1693247 | Nov 2005 | CN |
| 1699230 | Nov 2005 | CN |
| 1759074 | Apr 2006 | CN |
| 1886348 | Dec 2006 | CN |
| 101316799 | Dec 2008 | CN |
| 101578240 | Nov 2009 | CN |
| 101583576 | Nov 2009 | CN |
| 101679106 | Mar 2010 | CN |
| 101689376 | Mar 2010 | CN |
| 102026929 | Apr 2011 | CN |
| 102089252 | Jun 2011 | CN |
| 102131740 | Jul 2011 | CN |
| 102149649 | Aug 2011 | CN |
| 102363567 | Feb 2012 | CN |
| 102393289 | Mar 2012 | CN |
| 102531384 | Jul 2012 | CN |
| 102690059 | Sep 2012 | CN |
| 102791646 | Nov 2012 | CN |
| 102815860 | Dec 2012 | CN |
| 102887650 | Jan 2013 | CN |
| 102898022 | Jan 2013 | CN |
| 102958855 | Mar 2013 | CN |
| 103058506 | Apr 2013 | CN |
| 103058507 | Apr 2013 | CN |
| 103068759 | Apr 2013 | CN |
| 103097319 | May 2013 | CN |
| 103282318 | Sep 2013 | CN |
| 103328396 | Sep 2013 | CN |
| 103338926 | Oct 2013 | CN |
| 103569015 | Feb 2014 | CN |
| 103648996 | Mar 2014 | CN |
| 103946166 | Jul 2014 | CN |
| 103987671 | Aug 2014 | CN |
| 104114503 | Oct 2014 | CN |
| 104379522 | Feb 2015 | CN |
| 104619665 | May 2015 | CN |
| 104736496 | Jun 2015 | CN |
| 105293901 | Feb 2016 | CN |
| 105753314 | Jul 2016 | CN |
| 107108345 | Aug 2017 | CN |
| 107848870 | Mar 2018 | CN |
| 108046589 | May 2018 | CN |
| 207671927 | Jul 2018 | CN |
| 109071316 | Dec 2018 | CN |
| 112011100664 | Dec 2020 | DE |
| 0132751 | Feb 1985 | EP |
| 0163873 | Dec 1985 | EP |
| 0700879 | Mar 1996 | EP |
| 0931028 | Jul 1999 | EP |
| 1291631 | Mar 2003 | EP |
| 1314704 | May 2003 | EP |
| 1593658 | Nov 2005 | EP |
| 2263979 | Dec 2010 | EP |
| 2397449 | Dec 2011 | EP |
| 2415724 | Feb 2012 | EP |
| 2531459 | Dec 2012 | EP |
| 2540682 | Jan 2013 | EP |
| 2594536 | May 2013 | EP |
| 2609047 | Jul 2013 | EP |
| 2646243 | Oct 2013 | EP |
| 2666756 | Nov 2013 | EP |
| 2695734 | Feb 2014 | EP |
| 2736855 | Jun 2014 | EP |
| 2762459 | Aug 2014 | EP |
| 2762460 | Aug 2014 | EP |
| 3204338 | Aug 2017 | EP |
| 1012367 | Dec 1965 | GB |
| 1026770 | Apr 1966 | GB |
| 1089912 | Nov 1967 | GB |
| 1105433 | Mar 1968 | GB |
| 1334828 | Oct 1973 | GB |
| 47-004192 | Sep 1972 | JP |
| 54-083923 | Jul 1979 | JP |
| 62-187140 | Aug 1987 | JP |
| 02-293345 | Dec 1990 | JP |
| 07-263318 | Oct 1995 | JP |
| 11-328601 | Nov 1999 | JP |
| 2000-203872 | Jul 2000 | JP |
| 2000-327365 | Nov 2000 | JP |
| 2001-076336 | Mar 2001 | JP |
| 2001-354446 | Dec 2001 | JP |
| 2002-115071 | Apr 2002 | JP |
| 2002-174810 | Jun 2002 | JP |
| 2002-358626 | Dec 2002 | JP |
| 2003-505327 | Feb 2003 | JP |
| 2003-283028 | Oct 2003 | JP |
| 2004-099370 | Apr 2004 | JP |
| 2004-259402 | Sep 2004 | JP |
| 2005-062592 | Mar 2005 | JP |
| 2005-139031 | Jun 2005 | JP |
| 2005-519997 | Jul 2005 | JP |
| 2005-206406 | Aug 2005 | JP |
| 2005-289683 | Oct 2005 | JP |
| 2005-289685 | Oct 2005 | JP |
| 2005-320234 | Nov 2005 | JP |
| 2006-228431 | Aug 2006 | JP |
| 2007-527354 | Sep 2007 | JP |
| 2007-252589 | Oct 2007 | JP |
| 2007-255139 | Oct 2007 | JP |
| 2007-255319 | Oct 2007 | JP |
| 2007-314521 | Dec 2007 | JP |
| 2008-007384 | Jan 2008 | JP |
| 2008-094713 | Apr 2008 | JP |
| 2008-115071 | May 2008 | JP |
| 2009-084076 | Apr 2009 | JP |
| 2009-099239 | May 2009 | JP |
| 2009-107878 | May 2009 | JP |
| 2009-274902 | Nov 2009 | JP |
| 2009-280478 | Dec 2009 | JP |
| 2010-202514 | Sep 2010 | JP |
| 2011-057504 | Mar 2011 | JP |
| 2011-213576 | Oct 2011 | JP |
| 2011-527661 | Nov 2011 | JP |
| 2011-530470 | Dec 2011 | JP |
| 2012-066995 | Apr 2012 | JP |
| 2012-232882 | Nov 2012 | JP |
| 2013-502371 | Jan 2013 | JP |
| 2013-028512 | Feb 2013 | JP |
| 2013-035721 | Feb 2013 | JP |
| 2013-518800 | May 2013 | JP |
| 2013-520388 | Jun 2013 | JP |
| 2013-529172 | Jul 2013 | JP |
| 2013-533838 | Aug 2013 | JP |
| 2013-536155 | Sep 2013 | JP |
| 2013-542159 | Nov 2013 | JP |
| 2013-544227 | Dec 2013 | JP |
| 2014-012611 | Jan 2014 | JP |
| 2014-501214 | Jan 2014 | JP |
| 2014-073953 | Apr 2014 | JP |
| 5483923 | May 2014 | JP |
| 2014-136751 | Jul 2014 | JP |
| 2014-141363 | Aug 2014 | JP |
| 2014-522798 | Sep 2014 | JP |
| 2015-511537 | Apr 2015 | JP |
| 2015-511573 | Apr 2015 | JP |
| 2017-502188 | Jan 2017 | JP |
| 2017-502202 | Jan 2017 | JP |
| 10-1181342 | Sep 2012 | KR |
| 10-2012-0128657 | Nov 2012 | KR |
| 10-2013-0100235 | Sep 2013 | KR |
| 10-1302664 | Sep 2013 | KR |
| 1302664 | Sep 2013 | KR |
| 10-1328832 | Nov 2013 | KR |
| 10-2013-0135840 | Dec 2013 | KR |
| 10-2014-0131558 | Nov 2014 | KR |
| 10-1506378 | Mar 2015 | KR |
| 10-2016-0080048 | Jul 2016 | KR |
| 10-2021-0149192 | Dec 2021 | KR |
| 2127711 | Mar 1999 | RU |
| 187326 | Feb 2013 | SG |
| 1677028 | Sep 1991 | SU |
| 200911718 | Mar 2009 | TW |
| 201040118 | Nov 2010 | TW |
| 201313635 | Apr 2013 | TW |
| 201331148 | Aug 2013 | TW |
| 201335092 | Sep 2013 | TW |
| 201341324 | Oct 2013 | TW |
| 201350449 | Dec 2013 | TW |
| 201402490 | Jan 2014 | TW |
| 201520178 | Jun 2015 | TW |
| 9906334 | Feb 1999 | WO |
| 2000047529 | Aug 2000 | WO |
| 0107374 | Feb 2001 | WO |
| 2005042423 | May 2005 | WO |
| 2005091021 | Sep 2005 | WO |
| 2005093720 | Oct 2005 | WO |
| 2009041348 | Apr 2009 | WO |
| 2009041618 | Apr 2009 | WO |
| 2010002477 | Jan 2010 | WO |
| 2010005578 | Jan 2010 | WO |
| 2010014163 | Feb 2010 | WO |
| 2010016928 | Feb 2010 | WO |
| 2010147650 | Dec 2010 | WO |
| 2011022661 | Feb 2011 | WO |
| 2011041484 | Apr 2011 | WO |
| 2011069338 | Jun 2011 | WO |
| 2011077756 | Jun 2011 | WO |
| 2011085190 | Jul 2011 | WO |
| 2011097314 | Aug 2011 | WO |
| 2011103798 | Sep 2011 | WO |
| 2011103799 | Sep 2011 | WO |
| 2011104035 | Sep 2011 | WO |
| 2011149740 | Dec 2011 | WO |
| 2011149811 | Dec 2011 | WO |
| 2011149812 | Dec 2011 | WO |
| 2012027660 | Mar 2012 | WO |
| 2012074983 | Jun 2012 | WO |
| 2012126394 | Sep 2012 | WO |
| 2013016157 | Jan 2013 | WO |
| 2013018774 | Feb 2013 | WO |
| 2013027651 | Feb 2013 | WO |
| 2013028492 | Feb 2013 | WO |
| 2013032890 | Mar 2013 | WO |
| 2013047679 | Apr 2013 | WO |
| 2013074779 | May 2013 | WO |
| 2013082246 | Jun 2013 | WO |
| 2013088856 | Jun 2013 | WO |
| 2013110721 | Aug 2013 | WO |
| 2013116420 | Aug 2013 | WO |
| 2013120721 | Aug 2013 | WO |
| 2013130653 | Sep 2013 | WO |
| 2013130665 | Sep 2013 | WO |
| 2013130721 | Sep 2013 | WO |
| 2013136013 | Sep 2013 | WO |
| 2013184205 | Dec 2013 | WO |
| 2014042244 | Mar 2014 | WO |
| 2014052229 | Apr 2014 | WO |
| 2014097623 | Jun 2014 | WO |
| 2014100432 | Jun 2014 | WO |
| 2014175144 | Oct 2014 | WO |
| 2014180679 | Nov 2014 | WO |
| 2015057552 | Apr 2015 | WO |
| 2015057555 | Apr 2015 | WO |
| 2015077179 | May 2015 | WO |
| 2015080043 | Jun 2015 | WO |
| 2015127483 | Aug 2015 | WO |
| 2015175595 | Nov 2015 | WO |
| 2015195419 | Dec 2015 | WO |
| 2015195465 | Dec 2015 | WO |
| 2016014937 | Jan 2016 | WO |
| 2016028554 | Feb 2016 | WO |
| 2016057787 | Apr 2016 | WO |
| 2016070048 | May 2016 | WO |
| 2016073539 | May 2016 | WO |
| 2016174825 | Nov 2016 | WO |
| 2016185934 | Nov 2016 | WO |
| 2016191676 | Dec 2016 | WO |
| 2017030736 | Feb 2017 | WO |
| 2017100646 | Jun 2017 | WO |
| 2017177109 | Oct 2017 | WO |
| 2017177114 | Oct 2017 | WO |
| Entry |
|---|
| “Building Materials”, Co-edited by Xi'an University of Architecture and Technology, China Construction Industry Press, Edition 3, Apr. 30, 2004, 5 pages. |
| Abrams et al; “Fracture behavior of engineered stress profile soda lime silicate glass”; Journal of Non-Crystalline Solids; 321, (2003) 10-19. |
| Aegerter et al “Sol-gel technologies for glass producers and users—Chapter 4.1.8—Scratch resistant coatings (G. Helsch and G. H. Frischat)”, pp. 217-221, Kluwer Academic Publishers, 2004. |
| ASTM C1279-13 “Standard Test Method for Non-Destructive Photoelastic Measurement of Edge and Surface Stresses in Annealed, Heat-Strengthened, and Fully Tempered Flat Glass”; Downloaded Jan. 24, 2018; 11 Pages. |
| ASTM C1422/C1422M-10 “Standard Specification for Chemically Strengthened Flat Glass”; Downloaded Jan. 24, 2018; 5 pages. |
| ASTM C158-02(2012), Standard Test Methods for Strength of Glass by Flexure (Determination of Modulus of Rupture), ASTM International, West Conshohocken, PA, 2012, 9 pages. |
| Bahlawane “Novel sol-gel process depositing a-Al2O3 for the improvement of graphite oxidation-resistance”—Thin Solid Films, vol. 396, pp. 126-130, 2001. |
| Bansal et al; “Chapter 10: Elastic Properties” Handbook of Glass Properties; Elsevier; (1986) pp. 306-336. |
| Bansal et al; “Handbook of Glass Properties”; Elsevier; (1986) 2 pages. |
| Barnett Technical Services, “Surface Stress Meters”, Available Online at <https://web.archive.org/web/20200925054825/https://barnett-technical.com/luceo/surface-stress/>, Retrieved on Sep. 25, 2020, 4 pages. |
| Bouyne et al; “Fragmentation of thin chemically tempered glass plates”; Glass Technol., 2002, 43C, 300-2. |
| Brandt et al; “Mechanics of Ceramics, Active Materials, Nanoscale Materials, Composites, Glass, and Fundamentals”; Proceedings of the 8th International Symposium on Fracture Mechanics of Ceramics, (2003); 11 Pages. |
| Brunkov et al; “Submicron-Resolved Relief Formation in Poled Glasses and Glass-Metal Nanocomposites”; Technical Physics Letters, 2008, vol. 34, No. 12 pp. 1030-1033. |
| Bubsey, R.T. et al., “Closed-Form Expressions for Crack-Mouth Displacement and Stress Intensity Factors for Chevron-Notched Short Bar and Short Rod Specimens Based on Experimental Compliance Measurements,” NASA Technical Memorandum 83796, pp. 1-30 (Oct. 1992). |
| ChemCor Product Specification, 1990. |
| Corning Incorporated, “What Makes ChemCor Glass Work?” ChemCor Product Specification, Feb. 1990, 2 pgs. |
| Corning leads $62M Investment in ‘smart’ glass maker view, Jun. 19, 2013; http://optics.org/news/4/6/27. |
| Corning, “Nook—Stress Profile Measurement”, Corning Incorporated, 2019, 4 slides. |
| Declaration of Rostislav V. Roussev; 9 Pages; Aug. 11, 2019. |
| Dessler et al; “Differences between films and monoliths of sol-gel derived aluminas”, Thin Solid Films, vol. 519, pp. 42-51, 2010. |
| Donald “Review Methods for Improving the Mechanical Properties of Oxide Glasses”; Journal of Materials Science 24 (1989) 4177-4208. |
| Dusil J. and Strnad Z., “Black colored glass ceramics based on beta-quartz solid solutions,” Glass 1977: proceedings of the 11th International Congress on Glass, Prague, Czechoslovakia, Jul. 4-8, 1977, vol. 2, p. 139-149. |
| F.V. Tooley; “The Handbook of Glass Manufacture, vol. II”; China Architecture & Building Press, First Edition, Feb. 1983, pp. 304-305. |
| Fu, et al, “Preparation of alumina films from a new sol-gel route” Thin Solid films 348, pp. 99-102 (1999). |
| Glass Technology, Chapter 09, retrieved on Feb. 1, 2021, pp. 146-158 (Original Document Only). |
| Glover, D., Miller, D., Averis, D., Door, V. (2005) “The interactive whiteboard: a literature survey”. Technology, Pedagogy and Education (vol. 14) 2005, Issue 2: 155-170. |
| Greaves et al; “Inorganic Glasses, glass-forming liquids and amorphizing solids” Advances in Physics; vol. 56, No. 1; 2007 pp. 1-166. |
| Green; “Section 2. Residual stress, brittle fracture and damage; Critical parameters in the processing of engineered stress profile glasses”; Journal of Non-Crystalline Solids, 316 (2003) 35-41. |
| Gulati, “Frangibility of tempered soda-lime glass sheet” Glass Processing Days, Sep. 13-15, 1997. pp 72-76. |
| Guo et al., “Nucleation and Crystallization Behavior of Li2O—Al2O3—SiO2 System Glass-Ceramic Containing Little Fluorine and No-Fluorine”, J.Non-Cryst. Solids, 2005, vol. 351, No. 24-26, pp. 2133-2137. |
| Hampshire; “Oxynitride glasses, their properties and crystallization—a review”; Journal of Non-Crystalline Solids; vol. 316, 2003; pp. 64-73. |
| Hauk “Sol-gel preparation of scratch-resistant Al2O3 coatings on float glass”, Glass Science and Technology: Glastechnische Berichte, 72(12), pp. 386, 1999. |
| Inaba et al., “Non-destructive Stress Measurement In Double Ion-Exchanged Glass Using Optical Guided-Waves and Scattered Light”, Journal of the Ceramic Society of Japan 2017, vol. 125, No. 11, pp. 814-820. |
| Kim Yong-Hwan, “Glass Reinforcement by Ion Exchange Method (ReSEAT Program)”, Available Online at <http://www.reseat.re.kr>, Korea Institute of Science and Technology Information, retrieved in 2021, pp. 1-6 (Original Document Only). |
| Kim; “Glass Engineering”; Glass Technology 3rd Edition; (2009) 8 Pages. |
| Kitaigorodskii et al, In: Sb.Nauchn.Rabot Belor.Politekhn.Inst.,Khimiya, Tekhnologiya i Istoriya Stekla i Keramiki, 1960, No. 86, p. 38. (The Synthesis of Thermo-stable glasses) Abstract Only. |
| Le Bourhis; “Glass Mechanics and Technology”; Wiley-VCH, Second Edition; (2014) 8 Pages. |
| Le Bourhis; “Hardness”; Glass Mechanics and Technology; 2008; pp. 170-174. |
| Liu et al, “Common Knowledge Evidence: Inorganic Non-Metallic Materials Technology”, China University of Science and Technology Press, Sep. 2015, 1st edition. |
| Nagashima; “Chemical Strengthening of Glass”; Surface Technology; vol. 64, No. 8; (2013) pp. 434-438. |
| Peitl et al; “Thermal Shock Properties of Chemically Toughened Borosilicate Glass”; Journal of Non-Crystallin Solids, 247, (1999) pp. 39-49. |
| Poumellec et al; “Surface topography change induced by poling in Ge doped silica glass films”; 2003 OSA/BGPP 2003 MD 38. |
| Reddy et al. “Fracture Toughness Measurement of Glass and Ceramic Materials Using Chevron-Notched Specimens” J. Am. Ceram. Soc. 71 (6) C-310-C313 (1988). |
| Reseat, Available Online at <https://www.reseat.or.kr/static/view/forPrint.jsp?siteld=portal>, Retrieved on Jan. 19, 2021, 1 page (Original Document Only). |
| Rukmani et al., “Effects of V and Mn Colorants on the Crystallization Behavior and Optical Properties of Ce-Doped Li-Disilicate Glass”, in Journal of American Ceramic Society, vol. 90, 2007, pp. 706-711. |
| Rusan et al; “A New Method for Recording Phase Optical Structures in Glasses”; Glass Physics and Chemistry, 2010, vol. 36, No. 4, pp. 513-516. |
| Sglavo & Green, “Flaw-insensitive ion-exchanged glass: 11, Production and mechanical performance” J. Am. Ceram. Soc. 84(8) pp. 1832-1838 (2001). |
| Sglavo et al. “procedure for residual stress profile determination by curvature measurements” Mechanics of Materias, 2005, 37(8) pp. 887-898. |
| Shen et al; “Control of concentration profiles in two step ion exchanged glasses”; Phys. Chem. Glasses, 2003 44 (4), 284-92. |
| Shen et al; “Variable-temperature ion-exchanged engineered stress profile (ESP) glasses”; J. Am. Ceram. Soc., 86 [11] 1979-81 (2003). |
| Smedskjaer “Effect of thermal history and chemical composition on hardness of silicate glasses”; Journal of Non-Crystalline Solids 356 (2010); pp. 893-897. |
| Stosser et al “Magnetic Resonance investigation of the process of corundum formation starting from sol-gel precursors”, J. Am. Ceram. Soc, vol. 88, No. 10, pp. 2913-2922, 2005. |
| Takagi et al; “Electrostatic Imprint Process for Glass”; Applied Physics Express 1 (20008) 024003. |
| Tang et al. “Methods for measurement and statistical analysis of the frangibility of strengthened glass” Frontiers in Materials, 2015 vol 2, article 50. 8 pgs. |
| Tang, et al., “Automated Apparatus for Measuring the Frangibility and Fragmentation of Strengthened Glass”, Experimental Mechanics (Jun. 2014) vol. 54 pp. 903-912. |
| Varshneya, “Chemical Strengthening of Glass: Lessons Learned and Yet to be Learned”, International Journal of Applied Glass Science, vol. 1, No. 2, 2010, pp. 131-142. |
| Varshneya; “Fundamentals of Inorganic Glasses”; 2nd edition, Society of Glass Technology, 2006, pp. 513-521, XP002563094. |
| Varshneya; “Microhardness vs. Glass Composition”; Fundamentals of Inorganic Glasses; 2006; p. 208, paragraph 7. |
| Yong-Hwan; “Chemical Tempered Glass for Mobile Displays; Korea Institute of Science and Technology; 2020; 6 Pages”. |
| Zheng et al., “Structure and Properties of the Lithium Aluminosilicate Glasses with Yttria Addition”, Wuhan University of Technology, vol. 22, No. 2, 2007, pp. 362-366. |
| Zheng et al; “Effect of Y203 addition on viscosity and crystallizationof the lithium aluminosilicate glasses”; Thermochimica Acta 456 (2007) 69-74. |
| Zimmer, “Thin Glasses for Touch Display Technologies” Schott: glass made of ideas. Emerging Display Technologies Conference, Aug. 16-17, 2011. 17 slides. |
| Number | Date | Country | |
|---|---|---|---|
| 20230348322 A1 | Nov 2023 | US |
| Number | Date | Country | |
|---|---|---|---|
| 62366338 | Jul 2016 | US | |
| 62320077 | Apr 2016 | US |
| Number | Date | Country | |
|---|---|---|---|
| Parent | 17695948 | Mar 2022 | US |
| Child | 18212661 | US | |
| Parent | 16797638 | Feb 2020 | US |
| Child | 17695948 | US | |
| Parent | 16027741 | Jul 2018 | US |
| Child | 16797638 | US | |
| Parent | 15482213 | Apr 2017 | US |
| Child | 16027741 | US |
