Patent Application
20240217871
The present disclosure relates to the field of microcrystalline glass, and more particularly, to a low-warpage strengthened microcrystalline glass, a preparation method therefor, and an application thereof.
With the rapid development of the smart industry, especially when the 5G era comes, glass materials have played an increasingly important role in the field of portable mobile electronic devices. Since the wavelengths of electromagnetic waves used in 5G and even subsequent 6G communications are getting shorter and shorter, the requirements for materials used in communication equipment are therefore getting higher and higher, and the scope of glass used in communication equipment is also becoming wider and wider. Taking mobile phones as an example, it only takes less than 5 years to develop mobile phones from the early application of the front cover to the current dual application of the front and rear covers. It is foreseeable that within the next five years in the future, mobile phones with all-glass shells will likely appear.
Since the original property of glass is a brittle material with poor ductility, therefore, as a structural material of mobile phone, the requirement of dimensional accuracy is particularly high. After the glass itself is processed by a two-step treatment of 3D hot bending and chemical strengthening, there will be a significant scaling and warping phenomenon of dimension. At present, the mainstream NAS Glass and LAS Glass in the field of electronic glass use the method of high compressive stress (CS) on the surface and large Depth of layer (Dol) inside to improve the impact resistance of the strengthened glass. The stress distribution is generally composed of the following:
A prior art discloses a microcrystalline glass product with improved stress distribution, which emphasizes that on the stress distribution, there is an inflection point at a certain depth, and the slope |k| of the compressive stress curve is very large from the surface of the glass to the depth of the inflection point, as shown in
The present disclosure provides a low-warping strengthened (tempered) microcrystalline glass, and the microcrystalline glass is provided with a compressive stress layer extending from a surface to an interior of the glass, wherein a compressive stress on the surface of the glass is represented as CS<550 MPa, and the compressive stress has the following stress distributions:
Optionally, the compressive stress on the surface of the glass is represented as CS<350 MPa.
Optionally, k1 is represented as 2.45<|k1|<4.35.
Optionally, k1 is represented as 2.60<|k1|<3.75.
Optionally, k2 is represented as 1.00<|k2|<1.35.
Optionally, a depth of the compressive stress layer Dol_zero is represented as 110 μm-142 μm; and when the layer depth is 50 μum, the stress CS_50 is 60 MPa-130 MPa.
Optionally, a composition (wt %) of the microcrystalline glass is: SiO2 58.1%-78.8%, Al2O3 5.4%-24.1%, MgO+ZnO 0-15%, B2O3 0-3.3%, P2O5 0-1.9%, ZrO2 0-3.5%, Li2O 1.6%-13.7%, Na2O 1.6%-4.5%, K2O≤3.1%, Y2O3≤8%, and residuals are unavoidable impurities, wherein Na2O/R2O≤0.6, R2O/Al2O3≤5.25, and R2O is an alkali metal oxide.
Optionally, a crystal phase of the microcrystalline glass comprises one or more of lithium disilicate, lithium petalite, B-quartz solid solution, and spinel, wherein crystallinity is 70% to 98%.
Optionally, the crystallinity of the microcrystalline glass is 80% to 95%.
Optionally, the crystallinity of the microcrystalline glass is 87% to 95%.
Optionally, amount of warpage of the strengthened microcrystalline glass does not exceed 180 μm.
Optionally, the amount of warpage of the strengthened microcrystalline glass does not exceed 150 μm.
Optionally, the amount of warpage of the strengthened microcrystalline glass does not exceed 120 μm.
The present disclosure provides a preparation method for the strengthened microcrystalline glass as mentioned above, comprising steps of:
Optionally, the ion exchange in step 2 comprises a two-time ion exchanges, wherein:
Optionally, a content of KNO3 in the second molten salt bath is greater than or equal to 90 wt %, and a content of LiNO3 is represented as: 0<LiNO3≤0.15 wt %.
Optionally, the crystallization treatment in step 1 comprises the steps of: putting the base glass into a box-type crystallization furnace to perform a three-stage thermal treatment, wherein a first step is to raise the temperature to 520 to 580 Celsius degrees and keep the temperature for 200 to 300 minutes, a second step is to raise the temperature to 600 to 640 Celsius degrees and keep the temperature for 100 to 150 minutes, and a third step is to raise the temperature to 645 to 740 Celsius degrees and keep the temperature for 180 to 270 minutes; and then cooling down the base glass to obtain the basic microcrystalline glass.
The present disclosure further provides an application of the strengthened microcrystalline glass as mentioned above, wherein the strengthened microcrystalline glass is used as a cover plate for a mobile phone, a cover plate for a tablet computer, a cover plate for a watch, and a cover plate for a car display.
In order to describe the technical solutions in the embodiments of the present disclosure more clearly, the accompanying drawings required for describing the embodiments of the present disclosure are briefly introduced in the following. It should be understood that the following drawings illustrate only certain embodiments of the present disclosure and are therefore not to be considered limiting of the scope. For a person of ordinary skill in the art, other related drawings may also be obtained according to these drawings without creative efforts.
In order to make the purpose, technical solutions, and advantages of the embodiments of the present disclosure clearer, the technical solutions in the embodiments of the present disclosure will be clearly and completely described below. The elements that are not indicated by the specific conditions in the embodiments will be carried out according to the conventional conditions or the conditions suggested by the manufacturer. The reagents or instruments used that are not indicated by the manufacturer, are all conventional products that could be purchased from the market.
The present disclosure is for solving the warping problem that is easy to occur in the strengthening process, and the mode of solving deformation on the market at present all belongs to the mode of “pollution first, treatment later”, for example, for repairing deformation by a single-sided polishing, although the deformation may be repaired to a certain extent, but part of the strength brought by strengthening is sacrificed by polishing. The present disclosure fundamentally solves, from the perspectives of the internal structure and composition of the glass, the problem of easy deformation after strengthening.
In order to overcome the shortcomings of the prior art as mentioned above, the purpose of the present disclosure is to provide a low-warping strengthened microcrystalline glass, a preparation method therefore, and an application thereof. The CS on the surface of the prepared microcrystalline glass is low, and the compressive stress gradient difference is, extending from the surface to the interior of the glass, small and relatively uniform, which may significantly improve the warping problem caused by excessive compressive stress gradient difference after strengthening. Meanwhile, because the CT integral of the present disclosure is not weaker than that of the ordinary strengthened glass, plus the strength gain effect brought by the crystal, the overall drop resistance strength is even better than that of the ordinary strengthened glass.
The low-warping strengthened microcrystalline glass of the embodiments of the present disclosure, the preparation method therefore, and the application thereof are described below.
Some of the embodiments of the present disclosure provide a low-warping strengthened microcrystalline glass, wherein the amount of warpage of the low-warping strengthened microcrystalline glass does not exceed 180 μm, optionally, the warping volume does not exceed 150 μm, and optionally, the warping volume does not exceed 120 μm. In some embodiments, the microcrystalline glass is provided with a compressive stress layer extending from a surface to an interior of the glass, and a compressive stress on the surface of the glass is represented as CS<550 MPa. Optionally, the compressive stress CS may be 100 MPa-540 MPa, 130 MPa-500 MPa, 150 MPa-400 MPa, or 200 MPa-300 MPa, such as 500 MPa, 450 MPa, 400 MPa, 350 MPa, 320 MPa, 300 MPa, 280 MPa, 250 MPa, 180 MPa or 140 MPa, etc., or any value or range of values therebetween. Optionally, the compression stress on the surface of the glass is represented as CS<350 MPa. Optionally, CS<200 MPa. The compressive stress layer has the following stress distribution:
In some embodiments, the depth of the compressive stress layer Dol_zero is 110 μm-142 μm. Optionally, Dol_zero may be 115 μm-140 μm, 120 μm-135 μm or 125 μm-130 μm, such as 120 μm, 125 μm, 128 μm, 130 82 m, 135 μm, 138 μm or 140 μm, etc., or any value or range of values therebetween. In some embodiments, when the depth is 30 μm, the stress CS_30 is 65 MPa-455 MPa; optionally, CS_30 may be: 80 MPa-420 MPa, 100 MPa-380 MPa, 150 MPa-320 MPa or 200 MPa-250 MPa, such as 70 MPa, 75 MPa, 80 MPa, 85 MPa, 90 MPa, 95 MPa, 100 MPa, 105 MPa, 110 MPa, 115 MPa, 120 MPa, 125 MPa, 130 MPa, 135 MPa, 140 MPa, 150 MPa, 155 MPa, 160 MPa, 170 MPa, 180 MPa, 185 MPa, 190 MPa, 200 MPa, 220 MPa, 240 MPa, 250 MPa, 270 MPa, 300 MPa, 350 MPa, 370 MPa, 420 MPa or 440 MPa, etc., or any value or range of values therebetween; optionally, CS_30 is 100 MPa-300 MPa. In some embodiments, when the depth is 50 μm, the stress CS_50 is 60 MPa-130 MPa; optionally, CS_50 may be 70 MPa-120 MPa, or 80 MPa-110 MPa or 90 MPa-100 MPa, such as 65 MPa, 70 MPa, 75 MPa, 80 MPa, 85 MPa, 90 MPa, 95 MPa, 100 MPa, 105 MPa, 110 MPa, 115 MPa, 120 MPa or 125 MPa, etc., or any value or range of values therebetween; optionally, CS_50 is 80 MPa-110 MPa.
The strengthened microcrystalline glass of the present disclosure is provided with a compressive stress layer extending from the surface to the interior of the glass, the compressive stress on the surface is low, and there is no obvious stress inflection point, the depth of the compressive stress layer Dol_zero is 110 μm-142 μm. Through the compressive stress on the surface, the depth of the stress layer, and the control of the slope of the stress curve at the two depths of 0-30 μm and 30 μm-Dol_zero, the warping deformation of the glass caused by the large difference between the surface and internal stresses is reduced.
In some embodiment, the composition (wt %) of the microcrystalline glass is: SiO2 58.1%-78.8% (e.g. 60%-75%, 62%-70% or 64%-68%, such as 58.4%, 59%, 59.5%, 59.8%, 60% , 60.3%, 60.5%, 61%, 61.4%, 62%, 62.5%, 62.6%, 63%, 63.5%, 64%, 64.5%, 65%, 65.5%, 66%, 67.4%, 68%, 68.5%, 69%, 69.5%, 70%, 70.5%, 70.8%, 71%, 71.5%, 72%, 73%, 74%, 75%, 75.5%, 76%, 77% or 78%, etc., or any value or range of values therebetween), Al2O3 5.4%-24.1% (e.g. 6%-24%, 8%-20% or 10%-18%, such as 5.5%, 5.8%, 6%, 6.5%, 7%, 8% , 8.5%, 9%, 10%, 11%, 11.5%, 12%, 13%, 14%, 15%, 16%, 17%, 18%, 19%, 20%, 21%, 22%, or 23% etc., or any value or range of values therebetween), MgO+ZnO 0-15% (e.g. 1%-14%, 4%-12% or 6%-10%, such as 1%, 2%, 3%, 4%, 5%, 6%, 7%, 8%, 9%, 10%, 11%, 12%, 13% or 14%, etc., or any value or range of values therebetween), B2O3 0-3.3% (e.g. 0.1%-3.0%, 0.5%-2.5% or 1.0%-2.0%, such as 0.5%, 0.8%, 1%, 1.5%, 1.8%, 2%, 2.5%, 2.7% or 3.1%, etc., or any value or range of values therebetween), P2O5 0-1.9% (e.g. 0.1%-1.8%, 0.4%-1.5% or 0.8%-1.2%, such as 0.3%, 0.5%, 0.6%, 0.8%, 1.1%, 1.2%, 1.5% or 1.7%, etc.), ZrO2 0-3.5% (e.g. 0.1%-3.0%, 0.5%-2.5% or 1.0%-2.0%, such as 0.8%, 1%, 1.8%, 2.0%, 2.3%, 2.5%, 2.7%, 2.9%, 3.2%, or 3.4%, etc., or any value or range of values therebetween), Li2O 1.6%-13.7% (such as 2%-13%, 4%-10% or 6%-8%, Such as 1.8%, 2%, 2.4%, 2.8%, 3%, 3.5%, 4%, 4.5%, 5%, 6%, 7%, 8%, 9%, 10%, 11%, 12% or 13%, etc., or any value or range of values therebetween), Na2O 1.6%-4.5% (e.g. 2.0%-4.0%, 2.5%-3.5% or 2.8%-3.2%, such as 2%, 2.5%, 3%, 3.5% , 4% or 4.4%, etc., or 3.4%, etc., or any value or range of values therebetween), K2O≤3.1% (e.g. 0.19%-3.0%, 0.49%-2.8% or 1.09%-2.5%, such as 0.5%, 1%, 1.5%, 2%, 2.5% or 2.8%, etc., or any value or range of values therebetween), Y2O3 0-8% (e.g. 0.5%-7.5%, 2.5%-6.5% or 3.5%-5.5%, such as 1%, 2%, 3%, 4%, 5%, 6%, 7% or 7.5%, or any value or range of values therebetween), the balance is unavoidable impurities; where: Na2O/R2O≤0.6 (e.g. 0.05-0.58, 0.15-0.55 or 0.25-0.45, such as 0.1, 0.15, 0.2, 0.25, 0.3, 0.35, 0.4, 0.45, 0.5 or 0.55, or any value or range of values therebetween), R2O/Al2O3≤5.25 (e.g. 0.05-5.2, 0.1-5.0, 0.5-4.5, 1.0-4.0 or 2.0-3.0, such as 0.05, 0.1, 0.5, 0.8, 1.2, 1.3, 1.5, 2, 2.5, 3, 3.5, 4 , 4.5 or 5, etc., or any value or range of values therebetween), where R2O is a total proportion of alkali metal oxide.
Without being bound by theory, SiO2 is the main component that constitutes the network structure of microcrystalline glass and forms the crystal phase. It presents a silicon-oxygen tetrahedral structure in the glass, and has good chemical stability, thermal stability, and mechanical strength. In the present disclosure, the added amount of SiO2 is 58.1%-78.8%, optionally, the added amount of SiO2 is 60%-69%, and optionally, the added amount of SiO2 is 61%-67%.
Without being bound by theory, Al2O3 may constitute the network structure of the glass in the present disclosure, which may greatly improve the chemical stability and elastic modulus of the glass, and reduce the crystallization tendency of the glass. When Al exists as the structure of [AlO4] inside the glass, it acts as a part of the network structure, and connects with [SiO4] to form the network structure together with [SiO4], making the glass structure more compact. Since the molar volume of [AlO4] is larger than [SiO4], ions are easier to move in the glass body during ion exchange, which is more conducive to ion exchange; when Al exists as the structure of [AlO6] inside the glass, it is dissociated outside the network structure, and enriches the network structure in the form of network fillers, which increases the density of the network structure and Vickers hardness of the glass, and tamps the network structure. In the present disclosure, the added amount of Al2O3 is 5.4%-24.1%; optionally, the added amount of Al2O3 5.6-18%; optionally, the added amount of Al2O3 is 5.6-7.8%.
Without being bound by theory, MgO and ZnO, as optional components, has the effect of reducing the difficulty of melting of glass and improving the thermal stability of glass, and may also be used as crystal nucleating agents by taking advantage of their characteristics of easy phase separation. In the present disclosure, the added amount of MgO+ZnO is 0-15%, optionally, the added amount of both MgO and ZnO does not exceed 14%, wherein optionally, the added amount of MgO does not exceed 8.5%, and optionally, the added amount of ZnO does not exceed 10.5%.
Without being bound by theory, B2O3, as a network-formed oxide, has the effect of improving the melting characteristics of glass, and the appropriate content of B2O3 also has the effect of improving the strength and chemical durability of microcrystalline glass. In the present disclosure, the added amount of B2O3 is 0-3.3%, and optionally, the added amount is 1.5%-3%.
Without being bound by theory, P2O5 is added as the crystal nucleating agent in the present disclosure, and the added amount does not exceed 1.9%; optionally, the added amount does not exceed 1.5%; or no addition at all.
Without being bound by theory, ZrO2 has the effect of improving the stability of the glass, and also has the effect of refining grains and controlling the grain size during crystallization. In the present disclosure, the added amount does not exceed 3.5%; and optionally, the added amount does not exceed 2.5%.
Without being bound by theory, Alkali metal oxides Li2O, Na2O, K2O, etc., as the outer body of the network, have the effect of supplying oxygen, which may significantly reduce the melting temperature of the glass and adjust the viscosity-temperature characteristic of the glass. Li2O and Na2O are the main components of ion exchange. The added amount affects the ion exchange layer depth, surface stress, and stress distribution of the compressive stress layer of the microcrystalline glass products. In addition, Li2O also has the effect of promoting crystal formation and is a necessary component of the crystal phase composition. In the present disclosure, the added amount of Li2O is 1.6%-13.7%; optionally, the added amount of L2O is 2.5%-12.5%; and optionally, the added amount of Li2O is 5.8%-12.0%. The added amount of Na2O is 0.5%-4.5%; optionally, the added amount of Na2O is 1.6%-4.1%; and optionally, the added amount of Na2O is 1.7% -3.0%. The added amount of K2O does not exceed 3.1%; optionally, the added amount of K2O does not exceed 1.7%; and optionally, the added amount of K2O does not exceed 1.5%; or no addition at all.
Without being bound by theory, Y2O3 has the effect of tamping the network structure strength of microcrystalline glass and increasing Young's modulus. The inventors found that adding a certain amount of Y2O3 may also homogenize the stress distribution and reduce the possibility of warping, further ensuring the drop resistance strength and deformation stability of the product. In the present disclosure, the added amount of Y2O3 is 0-8%; optionally, the added amount of Y2O3 is 0.5%-4%; and optionally, the added amount of Y2O3 is 2%-4%.
The inventors find that by controlling the ratio of Na2O/R2O and R2O/Al2O3, the stress distribution in the compressive stress layer may be effectively homogenized and the warpage of the glass may be reduced. In the present disclosure, Na2O/R2O≤0.6; optionally, Na2O/R2O does not exceed 0.35; and optionally, Na2O/R2O does not exceed 0.25. The ratio of R2O/Al2O3≤5.25, wherein when the value is higher than 5.25, on the one hand, it may cause the network channel structure of the glass becomes small due to the content of Al is too low, which greatly affects the migration efficiency of ions in the network channel; on the other hand, it may affect the control of the type of the crystal phase, which may adversely affects the dimensional stability and optical properties of the glass. Optionally, R2O/Al2O3≤2.8; optionally, R2O/Al2O3≤2; optionally, R2O/Al2O3≤1.2; and optionally, R2O/Al2O3 ≤0.8.
In some embodiments, the crystal phase of the microcrystalline glass includes: one or more of lithium disilicate, lithium petalite, B-quartz solid solution, and spinel, wherein the crystallinity is 70%-98%, such as 85%-96%, 88%-95%, or 90%-93%, such as 70%, 74%, 78%, 80%, 82%, 84%, 86%, 88%, 90%, 91%, 92%, 93%, 94%, 95%, 96%, 97%, 98%, or any value or range of values therebetween. Theoretically, the higher the crystallinity, the smaller the possibility of warping deformation due to strengthening stress, because under the condition of a temperature lower than 500° C., the crystal does not participate in ion exchange, and the deformation mainly comes from the unbalanced stress on the two main surfaces after the strengthening of the residual glass phase, which causes the glass must change the area to achieve force balance (pressure P=F/S), that is, deformation occurs; but the higher the crystallinity, the less the residual glass phase, and it is mainly the glass phase that can participate in chemical ion exchange, so that the less the glass phase, the more limited the effect of toughening by chemical strengthening.
Therefore, it is necessary to find a balance between strength and dimensional stability, that is, to find a balance in the ratio distribution of the crystal phase and the glass phase. The inventors find that the best option for the glass phase is to be controlled within 5%-10%; optionally, the crystallinity is 80%-95%; and optionally, the crystallinity is 90%-95%. In terms of crystal phase selection, since there will be a process of transformation from lithium silicate crystal phase to lithium disilicate crystal phase during the crystallization process, it is necessary to control the proportion of residual lithium silicate crystal phase in the finished product, and it requires that the residual lithium silicate crystal phase is less than 5%, since too much lithium silicate crystal phase may significantly weaken the optical characteristics of the product, resulting in a bluish color of the product.
Some embodiments of the present disclosure also provide a preparation method for the strengthened microcrystalline glass, wherein in the aspect of preparing the base glass, melting and molding are performed by well-known methods in the art; and the formed base glass is crystallized and strengthened by the following steps:
In some embodiments, the crystallization treatment in step 1 includes the following steps: putting the base glass into a box-type crystallization furnace for a three-stage heat treatment, wherein the first step is to raise the temperature to 520° C.-580° C. (e.g. 530° C. , 540° C., 550° C., 560° C. or 570° C., etc.), and keep the temperature for 200 min-300 min (e.g. 220 min-280 min, 230 min-260 min or 240 min-250 min, such as 210 min, 220 min, 230 min , 240 min, 250 min, 260 min, 270 min, 280 min or 290 min, etc., or any value or range of values therebetween); the second step is to raise the temperature to 600-640° C. (e.g. 605° C.-635° C., 610° C.-630° C. or 615° C.-625° C., such as 600° C., 610° C., 620° C., 630° C., 635° C., 650° C. or 660° C., etc., or any value or value range therebetween), and keep the temperature for 100 min-150 min (e.g. 105 min-145 min, 110 min-140 min or 120 min-130 min, such as 110 min, 115 min, 120 min, 125 min, 130 min, 135 min, 140 min or 145 min, etc., or any value or range of values therebetween); and the third step is to raise the temperature to 645° C.-740° C. (such as 645° C., 650° C., 660° C., 690° C., 740° C., etc., or any value or range of values therebetween), and keep the temperature for 180 min-270 min (e.g. 190 min-260 min, 200 min-250 min or 210 min-240 min, such as 190 min, 200 min, 210 min, 220 min, 230 min, 240 min , 250 min or 260 min, etc., or any value or range of values therebetween); and then cooling down the base glass to obtain the basic microcrystalline glass.
Without being bound by theory, through the above-mentioned three-stage heat treatment process as mentioned above, on the one hand, the present disclosure may effectively control the crystallinity of the glass, and reduce, while ensuring the strength of the microcrystalline glass, the possibility of warping deformation caused by strengthening stress; and on the other hand, through the crystallization time at a high temperature above 645° C. being not less than 180 min, it can effectively control the glass crystal phase, reduce the proportion of residual lithium silicate crystal phase in the glass product, and prevent discoloration of the product.
In some embodiments, the ion exchange in step 2 includes two ion exchanges, including:
In some embodiments, the content of KNO3 in the second molten salt bath is greater than or equal to 90 wt % (e.g., 90 wt %-99.99 wt %, 92 wt %-98 wt % or 98 wt %-99.98 wt %, such as 92 wt %, 93 wt %, 94 wt %, 95 wt %, 96 wt %, 97 wt %, 98 wt %, 99 wt %, 99.2 wt %, 99.5 wt %, 99.7 wt %, 99.8 wt %, 99.9 wt %, 99.92 wt %, 99.95 wt %, 99.98 wt % or 99.99 wt %, etc., or any value or range of values therebetween), and the content of LiNO3 is represented as: 0<LiNO3≤0.15 wt % (e.g., 0.01 wt %-0.15 wt %, 0.04 wt %-0.12 wt % or 0.06 wt %-0.10 wt %, such as 0.02 wt %, 0.04 wt %, 0.05 wt %, 0.08 wt %, 0.1 wt %, 0.12 wt %, 0.13 wt % or 0.14 wt %, etc., or any value or range of values therebetween).
Without being bound by theory, after the base glass is processed by the crystallization process, the present disclosure obtains the strengthened microcrystalline glass with required stress distribution characteristics through the two-step ion exchange. In the first ion exchange (IOX1) process, the first molten salt bath contains at least 75% of NaNO3 salt, the exchange temperature is 430° C.-450° C., and the exchange time is 6 h-11h, so that the largest linear density of tensile stress may be formed in the first ion exchange process (CT_LD, ═Σ0CT_CVCT/Dol_zero), to maximize the strength of the glass. The first molten salt bath optionally does not contain potassium salt, even if it contains potassium salt, content of the potassium salt does not exceed 25 wt %, because the potassium salt contained in the molten salt bath may cause a large amount of K+ to adhere to the surface of the glass in IOX1. Since the radius of K+ is much larger than that of Na+ and Li+, it may greatly hinder the exchange of Na and Li, and ultimately may not achieve high strength. In the second ion exchange (IOX2) process, the content of KNO3 in the second molten salt bath is greater than or equal to 90 wt %, and a small amount of LiNO3 (0<LiNO3≤0.15 wt %) is contained, due to the small radius of Li+ and its high reactivity, the exchange rate of Li+ with Na+ on the surface of the glass is at least more than 3 times of the exchange rate of K+/Na+, so that the presence of a small amount of Li+ in the IOX2 salt bath may obviously inhibit the exchange reaction equilibrium to perform between K+ and Na+ on the surface of the glass in the salt bath, thereby avoiding the accumulation of K+ on the surface of the glass. The concentration distribution of K+ along the thickness direction is weakened, thereby reducing the surface compressive stress difference between the inner and outer layers of the glass, so that the obtained slop of stress curve changes more smoothly and naturally, and there is no obvious slope mutation (turning point). In terms of ion exchange time, a short-time exchange of less than or equal to 60 min is adopted. Through the control of the molten salt and exchange time as mentioned above, it may effectively prevent the compressive stress on the surface of the strengthened microcrystalline glass from being too high, prevent the stress difference within the distance per unit thickness from being too large, and reduce the glass warpage caused thereby. In addition, the compressive stress gradient difference of the obtained strengthened microcrystalline glass is small and relatively uniform. Compared with the current mainstream NAS Glass and LAS Glass, for the strengthened microcrystalline glass prepared by the present disclosure, when the depth of the stress layer is represented as 0μm≤Dol<30 μm, the absolute value |k1| of the stress curve between any two points separated by 20 μm on the curve is represented as: 2.45<|k1|<5.05; when the depth of the stress layer is represented as 30 μm≤Dol<Dol_zero, the absolute value |k2| of the slope of the stress curve between any two points separated by 20 μm on the curve is represented as 1≤|k2|≤1.5, wherein in the range of 0-30 μm, the slope is low, the area of the “trapezoid” formed by the stress curve and depth X and Y axes may be larger, the corresponding CT integral is not weaker than that of ordinary strengthened glass, and the overall drop resistance is even better than that of ordinary strengthened glass.
Various performance indicators of the microcrystalline glass products in the embodiments, examples, and comparative examples of the present disclosure are tested by the following method: using an SLP2000 stress tester (light source is 518 nm) produced by Japan Orihara Co., Ltd. for measurement. The crystal phase type and the crystallinity are detected by a method of XRD pulverization (Type: Shimadzu XRD-6100). Explanations of some terms in the present disclosure are as follows:
The strengthened microcrystalline glass of the present disclosure has a low surface CS, and the stress gradient difference, extending from the surface to a certain depth, is small and uniform, which may significantly improve the warping problem caused by excessive stress gradient differences after strengthening. The amount of warpage is less than or equal to 0.2 mm; meanwhile, because the CT integral of the microcrystalline glass of the present disclosure is not weaker than that of ordinary strengthened glass, and the strength gain effect brought by the crystal, the overall drop resistance strength is even better than that of ordinary strengthened glass. The B20 value of the drop height of the sandpaper surface of the crystal glass is represented as: B20≥1.3 m. The strengthened microcrystalline glass of the present disclosure has excellent warping resistance and may be widely used in the field of 3C electronic products.
In order to further clearly explain and illustrate the technical solution of the present disclosure, the following non-limiting embodiments are provided. Efforts have been made to ensure numerical accuracy in the embodiments of the present disclosure, but some errors and deviations must be considered. The composition itself is given in the percentage of weight (wt %) based on oxides and has been normalized to 100%, and the thickness of each sample in each of the embodiments is 0.65 mm.
Various performance indicators of the microcrystalline glass products in the following embodiments and comparative examples are tested using the methods described in the specific embodiments above.
Note: The sandpaper drop method is: using 176 g load, where the sandpaper is 180 mesh SiC sandpaper, performing a directional drop test from a height of 40 cm, dropping once at each height, increasing 10 cm each time, and recording the broken height.
Comparing Embodiments 1-16 and Comparative Examples 1-4, it can be seen that the CS on the surface of the glass in Embodiments 1-16 is low, and the stress curves are approximately linearly distributed. On the stress curves of 0-30 μm and 30-Dol_zero, the slope |k1| is represented as 2.4≤|k1|≤5.05, the slope |k2| is represented as 1.0≤|k2|≤1.5, and the compressive stress gradient difference thereof is small and relatively uniform. In terms of performance data of the prepared microcrystalline glass, the amount of warpage meets the application requirement of being less than or equal to 0.2 mm, and the B20 value of the drop height of the sandpaper surface meets the requirement of being greater than or equal to 1.3 m. Referring to Comparative Examples 1-4, it can be seen that the stress distribution characteristics of Comparative Example 1 are: on the stress curve of 30-Dol_zero layer depth, the slope |k2| is relatively large (1.7-3.0), and in the corresponding performance data of the prepared microcrystalline glass, although the amount of warpage is less than or equal to 0.15 mm, the performance is good, but the performance is poor in terms of the B20 value of the drop height of the sandpaper surface. The stress distribution characteristics of Comparative Example 2 are: on the stress curve of 0-30 μm layer depth, the slope |k1| is very large (12.8-19.0), in the corresponding performance data of the prepared microcrystalline glass, the amount of warpage is 0.18 mm-0.45 mm, the B20 of drop height of sandpaper surface is 0.93 m, and the performance is very poor. The stress distribution characteristics in Comparative Example 3 are: the depth of stress layer is Dol_zero (157 μm), slope |k1| is larger (5.2-6.8), |k2| is smaller (0.6-1.1), the drop resistance strength is poor (B20 is 0.92 m), and the warpage resistance performance is poor (the amount of warpage is 0.3 mm-0.6 mm). The stress distribution characteristics in Comparative Example 4 are: the depth of the stress layer Dol_zero is relatively large (162 μm), and in the corresponding performance data of the prepared microcrystalline glass, the warpage resistance performance is slightly poorer (0.22 μm-0.38 μm), and the drop resistance performance is poorer (B20 is 0.88 m).
In addition, from Comparison of Embodiments 11 and 14, it can be seen that when the preparation process is the same (including the crystallization process and ion exchange process), in terms of the composition of the microcrystalline glass, a lower R2O/Al2O3 ratio is selected, which is very important for obtaining a glass with low warpage, and the glass with better performance (i.e., lower warpage) may further be obtained.
From Comparison of Embodiments 12 and 13, it can be seen that when the glass composition and crystallization process are the same, in the ion exchange process, the salt bath of IOX1 does not contain K salt, which is beneficial for obtaining high-strength glass, and it may further obtain the glass with better performance (i.e., higher strength).
From Comparison of Embodiments 11-13, and 15 with Comparative Examples 1 and 3-4, it can be seen that, when the glass composition is the same, the temperatures of the third stage of the crystallization process in Embodiments 11-13 and 15 are within the temperature range of the present disclosure, which can avoid the occurrence of lithium silicate in the crystal phase of the microcrystalline glass, thereby further ensuring the excellent optical performance of the product; the temperatures in the third stage of the crystallization process in Comparative Examples 1 and 3-4 are too low, resulting in occurrence of lithium silicate in the crystal phase of the microcrystalline glass, which would obviously weaken the optical performance of the product.
The above are only the implementations of the present disclosure, and do not limit the patent scope of the present disclosure. Any equivalent structure or equivalent process conversion made by using the contents of the present disclosure and the accompanying drawings, or directly or indirectly used in other related technologies fields, are equally included in the patent protection scope of the present disclosure.
| Number | Date | Country | Kind |
|---|---|---|---|
| 202111110119.0 | Sep 2021 | CN | national |
This application is the continuation-in-part application of International Application No. PCT/CN2022/119442, filed on Sep. 16, 2022, which is based upon and claims priority to Chinese Patent Application No. 202111110119.0, filed on Sep. 18, 2021, the entire contents of which are incorporated herein by reference.
| Number | Date | Country | |
|---|---|---|---|
| Parent | PCT/CN2022/119442 | Sep 2022 | WO |
| Child | 18607566 | US |
