Patent Application
20240270627
The present disclosure relates to the field of microcrystalline glass (i.e., glass-ceramic), and in particular, to transparent microcrystalline glass, and a preparation method therefor and a use thereof.
With the arrival of intelligent era of mobile phones, the mobile phones have become an indispensable communication tool in daily life. As mobile phone users grow year by year, in order to meet requirements of the mobile phone users and increase use experience of the users, the mobile phones are also updated, transformed and phased out at an ever-increasing rate. The mobile phone cover glass develops from the earliest 2D glass to 2.5D glass and then to nowaday 3D glass, which adds novelty to terminal products of the mobile phones in appearance, and meanwhile also can enhance the users' sense of touch experience.
The reason why glass can be used as a cover plate for mobile phones is not only due to its good mechanical performance, but also due to its high transparency. Common glass has no change in optical performance when being subjected to a heat treatment. However, the microcrystalline glass, composed of a glass phase and a crystalline phase, will produce large and small crystals inside during heat treatment. The crystalline phases contained in the microcrystalline glass in different crystalline states have certain differences. Studies have shown that a difference in refractive index between the crystalline phase and the glass phase is a main cause for deterioration of the optical performance of the microcrystalline glass. For lithium-aluminum-silicate (LAS) microcrystalline glass (Li2O—Al2O3—SiO2 glass-ceramic, Li2O—Al2O3—SiO2 system glass-ceramic), lithium silicate (Li2SiO3) and β-quartz (β-SiO2) may deteriorate the optical performance of the microcrystalline glass, wherein lithium silicate (Li2SiO3) mainly appears in processes with low crystallinity and excessive crystallization, and β-quartz (β-SiO2) mainly appears in processes with excessive crystallization.
Microcrystalline glass with different crystalline states may be obtained through different heat treatment processes, and the microcrystalline glass with different crystalline states has certain difference in optical performance. During the heat treatment, abnormal crystallization of the microcrystalline glass inevitably exists, that is, the situation that a glass sheet is whitish occurs.
Therefore, how to obtain transparent microcrystalline glass with an excellent optical performance from the heat treatment is of great significance, which not only can improve the quality of the microcrystalline glass, but also can improve the production yield of the microcrystalline glass, thereby reducing the production cost.
For this purpose, the present disclosure aims at providing transparent microcrystalline glass, a preparation method therefor and a use thereof. For a crystallized glass raw sheet, the present disclosure, starting from a heat treatment process, obtains the microcrystalline glass with an XRD diffraction peak height H of ≥870 by controlling relevant process parameters. The prepared microcrystalline glass has an excellent optical performance, takes a short period of time, and has a high production yield and high production efficiency.
In the first aspect, the present disclosure provides a preparation method for transparent microcrystalline glass, wherein the method may include the following steps:
In some embodiments, a temperature of the nucleation may be Tg+10° C.˜Tg+80° C., and a duration of the nucleation is 120˜360 min.
In some embodiments, a temperature of the crystallization may be Tg+ΔT1, and a duration of the crystallization is 30˜150 min, where 100° C.≤ΔT1≤150° C.
In some embodiments, the XRD diffraction peak height H of the microcrystalline glass may be 960˜1150.
In some embodiments, processing durations of the k high-temperature stages, the n heating stages and the m cooling stages are each independently selected from 10˜90 s.
In some embodiments, in the n heating stages, a temperature difference between any two adjacent heat treatment stages is within a range of 10˜150° C.; and optionally, in the m cooling stages, a temperature difference between any two adjacent heat treatment stages is within a range of 10˜150° C.
In some embodiments, in the k high-temperature stages, a temperature difference between any two adjacent heat treatment stages is within a range of 5˜30° C., and preferably, the temperature difference is within a range of 10˜20° C.
In some embodiments, the glass raw sheet may be lithium-aluminum-silicate glass (lithium-aluminum-silicate system glass).
In some embodiments, the glass raw sheet may contain the following components in mol %:
In the second aspect, the present disclosure provides microcrystalline glass prepared by the above method, wherein an XRD diffraction peak height H of the microcrystalline glass is greater than or equal to 870, preferably 960˜1150, and further preferably 980˜1132.
Preferably, b value of the microcrystalline glass is less than or equal to 0.4.
Preferably, in the microcrystalline glass, a content of lithium disilicate and petalite is 90˜100%.
Preferably, in the microcrystalline glass, a content of crystalline phases of lithium silicate and β-quartz is 0-10%, wherein preferably, the content of the crystalline phases of lithium silicate and β-quartz is less than or equal to 5; and further preferably, the content of the crystalline phases of lithium silicate and β-quartz is 0.
In the third aspect, the present disclosure provides a use of the microcrystalline glass prepared by the above method, wherein the microcrystalline glass is used as any one of a mobile phone cover plate, a tablet computer cover plate, a watch cover plate, and an automobile display cover plate.
The present disclosure at least has the following beneficial technical effects.
The present disclosure, starting from the heat treatment process, divides the heat treatment into three stages, namely, the heating stage, the high-temperature stage and the cooling stage, and obtains the microcrystalline glass with the XRD diffraction peak height H of ≥870 by controlling the maximum value of the temperature in the high-temperature stages, Tmax=Tg+ΔT2, where the ΔT2 satisfies:
The microcrystalline glass prepared through this process has a good optical performance, and particularly when controlling the diffraction peak height H of the obtained microcrystalline glass to be 960-1150, the microcrystalline glass with the b value of ≤0.4 may be obtained. Moreover, this process improves the production yield of cover plates of the transparent microcrystalline glass, takes a short period of time, and has high production efficiency.
In order to more clearly illustrate technical solutions of examples of the present disclosure, a drawing that needs to be used in the related art and examples of the present disclosure is described briefly below. It should be understood that the drawing merely shows some examples of the present disclosure, and therefore should not be considered as a limitation to the scope. Those ordinarily skilled in the art could also obtain other relevant drawings according to the drawing without using any inventive efforts.
In order to make objectives, technical solutions and advantages of the examples of the present disclosure clearer, the technical solutions in the examples of the present disclosure will be described clearly and completely below. If no specific conditions are specified in the examples, they are carried out under normal conditions or conditions recommended by manufacturers. If manufacturers of reagents or apparatuses used are not specified, they are all commercially available conventional products.
Transparent microcrystalline glass, and a preparation method therefor and a use thereof in the examples of the present disclosure are specifically illustrated below.
The present disclosure provides a preparation method for transparent microcrystalline glass, wherein the method includes the following steps:
The heat treatment is divided into a heating stage, a high-temperature stage and a cooling stage. The heating stage is divided into n heating stages, which are N1, N2, N3 . . . Nn, respectively. The high-temperature stage is divided into k high-temperature stages, which are K1, K2, K3 . . . Kk, respectively. The cooling stage is divided into m cooling stages, which are M1, M2, M3 . . . Mm, respectively. The k is an integer obtained by rounding (n+k+m)/3, and 6≤n+k+m≤30.
During the heat treatment process, the heating stage and the cooling stage play a role of pre-heating and cooling the microcrystalline glass, because if the glass is directly placed in a high-temperature environment from a low-temperature environment or placed in a low-temperature environment from a high-temperature environment, the glass is likely to break due to uneven cold and heat of the glass itself caused thereby. The high-temperature stage belongs to a secondary crystallization stage of the microcrystalline glass, and after the k stages of high-temperature heat treatment, crystal growth in the microcrystalline glass is more mature, which is manifested in increased crystallinity of the microcrystalline glass. The inventor found through experiments that, for microcrystalline glass that is easy to experience devitrification, such as lithium-aluminum-silicate microcrystalline glass, a total number of stages of the heat treatment process may be small, and when 6≤n+k+m≤15, microcrystalline glass with crystallinity of greater than 90% can be obtained; and for microcrystalline glass that is difficult to experience devitrification, such as spinel microcrystalline glass, the number of stages of the heat treatment process may be appropriately increased, that is, when 15≤n+k+m≤30, microcrystalline glass with crystallinity of greater than 90% may be obtained; but when the number of stages of the heat treatment is greater than 30, as a state of obtained microcrystalline glass is almost the same as that of microcrystalline glass obtained when the number of stages of the heat treatment process is 30, it may be considered in this case that the precipitated crystal of the microcrystalline glass is already in a saturated state when the number of stages of the heat treatment process is increased to 30, and therefore, the total number of the stages of the heat treatment process is controlled within the range of 6≤n+k+m≤30 from efficiency and cost considerations.
Specifically, n+k+m may be 7, 8, 9, 10, 12, 14, 16, 18, 20, 21, 22, 25, 27, 28, etc. Preferably, the number of the heating stages and the number of the cooling stages are equal or similar. For example, when n+k+m=9, there are 9/3=3 high-temperature stages, and 3 heating stages and 3 cooling stages, respectively; when n+k+m=10, by rounding 10/3 to obtain an integer 3, there are 3 high-temperature stages, and there may be 3 heating stages and 4 cooling stages, or 4 heating stages and 3 cooling stages; and when n+k+m=11, by rounding 11/3 to obtain an integer 3, there are 3 high-temperature stages, and there may be 4 heating stages and 4 cooling stages, respectively.
Each high-temperature stage has a constant temperature TKi, where i=1, 2, 3 . . . ;
In the above, the ΔT2 satisfies the following formula:
Moreover, in the k high-temperature stages, a temperature difference between any two adjacent heat treatment stages is within a range of 5˜50° C. Specifically, the temperature difference may be 8° C., 10° C., 15° C., 18° C., 20° C., 25° C., 30° C., 35° C., 40° C., or 45° C., etc., preferably, the temperature difference is within a range of 5˜30° C., and further preferably, the temperature difference is within a range of 10˜20° C.
In some embodiments, a temperature of the nucleation is Tg+10° C.˜T9+80° C., and a duration of the nucleation is 120˜360 min. Specifically, the temperature of the nucleation may be Tg+20° C., Tg+30° C., Tg+40° C., T9+50° C., Tg+60° C., or Tg+70° C., etc.; and the duration of the nucleation is 130 min, 150 min, 180 min, 200 min, 240 min, 260 min, 300 min, 320 min or 340 min, etc.
In some embodiments, a temperature of the crystallization is Tg+ΔT1, and a duration of the crystallization is 30˜150 min, where 100° C.≤ΔT1≤150° C. Specifically, ΔT1 may be 110° C., 115° C., 120° C., 125° C., 130° C., 135° C., 140° C. or 145° C., etc.; and the duration of the crystallization may be 35 min, 40 min, 50 min, 60 min, 70 min, 80 min, 90 min, 100 min, 110 min, 120 min, 130 min or 140 min, etc.
The inventor found that, during the nucleation, crystallization and heat treatment of the glass, by setting different crystallization and heat treatment processes, the microcrystalline glass in different crystallization states may be obtained, and correspondingly, the XRD highest diffraction peak height of the microcrystalline glass also has a certain pattern of change.
During the crystallization and heat treatment, by adjusting the temperature ΔT1 during the crystallization treatment and the temperature ΔT2 in the high-temperature stage during the heat treatment, the microcrystalline glass with different XRD highest diffraction peak heights H may be obtained, and a relationship therebetween is as follows.
When the XRD highest diffraction peak height is less than 870:
When the XRD highest diffraction peak height is greater than 870:
In the above, the highest diffraction peak height H of the glass obtained during the crystallization treatment is less than 870. In combination with Formula I, a specific range of the diffraction peak height H may be determined by adjusting the magnitude of relevant parameter ΔT1 during the crystallization process. In this case, the crystal growth of the microcrystalline glass is not yet mature, the crystallinity of the microcrystalline glass is low, and the crystallinity y is less than or equal to 70%, that is, the glass in this state has poor transparency.
In order to further improve the transparency of the glass, the heat treatment needs to be performed on the crystallized glass, so as to improve the crystallinity of the microcrystalline glass. As the crystallinity y of the microcrystalline glass is greater than or equal to 70%, the crystal growth of the microcrystalline glass also gradually tends to be mature, the corresponding XRD highest diffraction peak height also starts to rise, the highest diffraction peak height H in this case is greater than or equal to 870, and the glass in this state needs to be obtained by increasing the temperature of the heat treatment. In combination with Formula 2, a specific range of the diffraction peak height H may be determined by adjusting the magnitude of relevant temperature parameter ΔT2 in the high-temperature stage in the heat treatment process.
The inventor further found that the XRD highest diffraction peak height and b value of the microcrystalline glass have a certain pattern of change.
Complete crystallization: in the microcrystalline glass, the lithium silicate (Li2SiO3) crystalline phase is completely converted into the lithium disilicate (Li2Si2O5) crystalline phase, and there are no (or less) lithium silicate (Li2SiO3) crystalline phase, β-quartz (β-SiO2) crystalline phase and other crystalline phases.
Excessive crystallization: the microcrystalline glass reaches the complete crystallization, and meanwhile lithium silicate (Li2SiO3), β-quartz (β-SiO2) and other crystalline phases are generated.
b value: it is a yellow-blue value. The b value is measured for transmitted light, wherein when the b value is positive, it indicates that less blue light is transmitted, that is, more blue light is reflected, and a larger b value indicates bluer glass.
In the present disclosure, in combination with Formula II:
by adjusting the value of the relevant process parameter ΔT2 of the high-temperature stage in the heat treatment process, a range of the XRD highest diffraction peak height of a cover plate of the microcrystalline glass after the heat treatment may be determined, and the peak height H thereof is made greater than 870, preferably within a range from 960 to 1150, thus the generation of crystalline phases of lithium silicate and β-quartz may be avoided to the greatest extent, so as to obtain a transparent microcrystalline glass cover plate with a good optical performance.
In some embodiments, processing durations of the k high-temperature stages, the n heating stages and the m cooling stages are each independently selected from 10˜90 s. Specifically, the processing durations may be 15 s, 20 s, 25 s, 30 s, 35 s, 40 s, 45 s, 50 s, 55 s, 60 s, 65 s, 70 s, 75 s, 80 s or 85 s, etc. By controlling the duration of each stage, while controlling the diffraction peak height and obtaining the microcrystalline glass with a good optical performance, the production duration consumed may be shortened, and the production efficiency may be improved.
In some embodiments, in the n heating stages, a temperature difference between any two adjacent heat treatment stages is within a range of 10˜150° C., wherein specifically, the temperature difference may be 15° C., 20° C., 30° C., 40° C., 50° C., 60° C., 70° C., 80° C., 90° C., 100° C., 110° C., 120° C., 130° C. or 140° C., etc. Optionally, in the m cooling stages, a temperature difference between any two adjacent heat treatment stages is within a range of 10˜150° C., wherein specifically, the temperature difference may be 15° C., 20° C., 30° C., 40° C., 50° C., 60° C., 70° C., 80° C., 90° C., 100° C., 110° C., 120° C., 130° C. or 140° C., etc.
In some embodiments, the glass raw sheet is lithium-aluminum-silicate glass. Preferably, the glass contains the following components (mol %): SiO2 65-72% (for example, 66%, 67%, 68%, 69%, 70% or 71%), Al2O3 3-7% (for example, 3.5%, 4%, 4.5%, 5%, 5.5%, 6% or 6.5%), ZrO2 0.5˜5% (for example, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4% or 4.5%), Li2O 15˜25% (for example, 16%, 17%, 18%, 19%, 20%, 21%, 22%, 23% or 24%), Na2O 0˜2% (for example, 0.1%, 0.8%, 1%, 1.2%, 1.5%, 1.8% or 1.9%), P2O5 0.5˜2% (for example, 0.7%, 0.9%, 1%, 1.2%, 1.5%, 1.8% or 1.9%), B2O3 0˜2% (for example, 0.1%, 0.5%, 1%, 1.2%, 1.5%, 1.8% or 1.9%), MgO 0˜3% (for example, 0.1%, 0.5%, 0.7%, 0.9%, 1%, 1.2%, 1.5%, 1.8%, 2.4%, 2.7% or 2.9%), ZnO 0˜3% (for example, 0.1%, 0.3%, 0.6%, 0.9%, 1%, 1.2%, 1.5%, 1.8%, 2%, 2.5% or 2.7%).
The present disclosure further provides microcrystalline glass prepared by the above method, wherein an XRD diffraction peak height H of the microcrystalline glass is greater than or equal to 870, preferably 960˜1150, and further preferably 980˜1132.
Preferably, b value of the microcrystalline glass is less than or equal to 0.4; and specifically, the b value may be 0.39, 0.38, 0.37, 0.36, 0.35, 0.34, 0.33, 0.32, 0.31 or 0.3, etc.
Preferably, in the microcrystalline glass, a content of lithium disilicate and petalite is 90-100%; and specifically, the content may be 91%, 93%, 94%, 95%, 97% or 99%, etc.
Preferably, in the microcrystalline glass, a content of crystalline phases of lithium silicate and β-quartz is 0-10%, wherein preferably, the content is less than or equal to 5; and further preferably, the content is 0.
The present disclosure further provides a use of microcrystalline glass prepared by the above method, wherein the microcrystalline glass is used as any one of a mobile phone cover plate, a tablet computer cover plate, a watch cover plate, and an automobile display cover plate.
In order to further clearly illustrate and explain the technical solutions of the present disclosure, non-limiting examples are provided below.
Glass raw materials were blended, so as to obtain glass expressed by mol % of oxides in Table 1. After the mixing, melting and molding were performed, wherein molding methods include a float method, overflowing, rolling, casting, etc. A molded glass plate was annealed, and then cut and polished, so as to obtain glass raw sheets with the same size. The prepared glass raw sheets each had a thickness of 0.58 mm±0.02 mm.
A glass transition temperature Tg in Table 1 was evaluated by a following method:
The obtained glass raw sheets were treated under conditions described in Tables 2-5. In columns of crystallization process in the tables, a magnitude of ΔT1 is described, wherein a crystallization temperature in specific implementation is Tg+ΔT1. In columns of heat treatment process in the tables, heat treatment regimens for glass 1 to glass 5 are described, wherein a magnitude of ΔT2 is equal to a highest heat treatment temperature in high-temperature stage minus the glass transition temperature Tg. In columns of crystal content in Tables 2-5, letters A, B, C, and D respectively represent crystalline phases of petalite, lithium disilicate, lithium silicate, and quartz. Meanwhile, the crystal content in Tables 2-5 represents a proportion of a mass of crystals indicated to a total mass of crystals in the glass.
A diffraction peak height, precipitated crystals, and b value of the glass in Tables 2-5 were evaluated by following methods:
The X-ray diffractometer used in the present disclosure is Shimadzu XRD-6100, and a range of incident angle used for test is 2 Theta=10-80°, a scan speed is 6°/min, a working voltage is 40 KV, and a working current is 30 KA.
The crystalline phases contained in the microcrystalline glass were analyzed using JCPDS card database in the JADE software.
Performance test result is described as follows.
In Examples 1-8, the glass raw sheets of the glass 1 were treated under different crystallization and heat treatment processes. In the above, Examples 1-6 had the same nucleation and crystallization processes and different heat treatment processes. The heat treatment processes mainly differed in that heat treatment temperatures in the high-temperature stages were different, that is, ΔT2 was different, wherein ΔT2 in Example 1 was the highest, the XRD highest diffraction peak height H after corresponding heat treatment was also the highest, reaching 1155, crystalline phases of the obtained glass contained lithium silicate appearing due to excessive crystallization, and the b value of the glass was 0.43, thus the optical performance was poor compared with several other examples. In addition, the diffraction peak height H in Example 6 was the lowest, and although the crystalline phases contained incompletely crystallized lithium silicate, etc., with a content of 2%, the b value of the glass was 0.38. It can be seen from comparison of Examples 1, 7, and 8 that under the same nucleation process, with the increase of the crystallization temperature, the XRD highest diffraction peak height H after the crystallization also increases.
In Examples 9-16, the glass raw sheets of the glass 2 were treated under different heat treatment processes. The heat treatment processes mainly differed in different ΔT2, wherein ΔT2 and the diffraction peak height H in Example 9 were the highest, lithium silicate also appeared in the crystalline phases, the b value of the glass exceeded 0.4, and thus the optical performance was poor compared with several other examples.
In Examples 17-22, the glass raw sheets of the glass 3 were treated under different heat treatment processes. The heat treatment processes mainly differed in different ΔT2, wherein ΔT2 and the diffraction peak height H in Example 17 were the highest, lithium silicate also appeared in the crystalline phases, and thus the optical performance was poor compared with several other examples.
In Examples 25-30, the glass raw sheets of the glass 4 were treated under different heat treatment processes. The heat treatment processes mainly differed in different ΔT2, wherein ΔT2 and the diffraction peak height H in Example 25 were the highest, lithium silicate also appeared in the crystalline phases, and thus the optical performance was poor compared with several other examples. Besides, ΔT2 and the diffraction peak height H in Example 30 were the lowest compared with several other examples, a content of residual incompletely crystallized lithium silicate in the crystalline phases was high and reached 1%, and the b value of the obtained glass was 0.38.
In Examples 33-38, the glass raw sheets of the glass 5 were treated under different heat treatment processes. The heat treatment processes mainly differed in different ΔT2, wherein ΔT2 and the diffraction peak height H in Example 33 were the highest, lithium silicate also appeared in the crystalline phases, and thus the optical performance was poor compared with several other examples.
The above are only embodiments of the present disclosure, and do not limit the patent scope of the present disclosure. All equivalent structure or equivalent flow transformations made by utilizing the contents of the description and the drawing of the present disclosure, which are directly or indirectly applied to other related technical fields, are similarly included in the scope of protection of the present disclosure.
| Number | Date | Country | Kind |
|---|---|---|---|
| 202110897039.8 | Aug 2021 | CN | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/CN2022/110155 | 8/4/2022 | WO |
