TW202417394A - Glass ceramic, glass ceramic product and manufacturing method thereof - Google Patents

Abstract

The invention provides a microcrystalline glass product which comprises the following components in percentage by weight: 40-60% of SiO2; 20 to 40 percent of Al2O3; li2O: 2%-15%; 3 to 20 percent of Na2O; the content of P2O5 + ZrO2 is 1 to 15 percent. Through reasonable component design, the obtained microcrystalline glass product has excellent mechanical properties, and can be applied to the fields of display equipment or electronic equipment and the like.

Description

Glass-ceramics, glass-ceramics products and manufacturing methods thereof

The present invention relates to a glass-ceramic, and in particular to a glass-ceramic with excellent mechanical properties, a glass-ceramic product and a manufacturing method thereof.

In recent years, with the continuous rise and development of consumer electronic products, glass, as a transparent material with good performance, has been widely used in such electronic devices. For example, LED and LCD displays and computer monitors, portable electronic products (such as mobile phones, tablet computers and personal media terminals, etc.), the glass used in them not only needs to be able to withstand the usual "touch" contact from the application for a long time, but also needs to be able to withstand the accidental bending, scratches and impacts that may occur during use, which puts higher requirements on the relevant performance of the glass.

Glass-ceramics is a material that is crystallized by heat treatment of glass. It has better mechanical properties than ordinary glass. The microcrystals formed in the glass have obvious advantages over ordinary glass in terms of bending resistance, wear resistance and drop resistance. On the other hand, the mechanical properties of glass-ceramics can be further improved by chemical strengthening. Based on the above advantages, glass-ceramics or glass-ceramics products obtained after treatment are currently used in display devices or electronic devices with high requirements for drop resistance, pressure resistance, scratch resistance, etc., especially in the front and back covers of portable electronic devices (such as mobile phones, watches, PADs, etc.).

Therefore, developing a glass-ceramic and glass-ceramic products with excellent mechanical properties suitable for display devices or electronic devices has become the goal pursued by scientific and technological personnel.

The technical problem to be solved by the present invention is to provide a microcrystalline glass and microcrystalline glass products with excellent mechanical properties.

(1) A glass-ceramic product, the components of which, expressed in weight percentage, include: SiO ₂ : 40-60%; Al ₂ O ₃ : 20-40%; Li ₂ O: 2-15%; Na ₂ O: 3-20%; P ₂ O ₅ +ZrO ₂ : 1-15%.

(2) The glass-ceramic product according to (1), further comprising, expressed in weight percentage, _K2O : 0-8%; and/or ZnO: 0-6%; and/or _B2O3 : 0-6%; and/or RO: _0-8 %; and/or _TiO2 : 0-5%; and/or _{Ln2O3 :} 0-5%; and/or clarifier: 0-2%, wherein RO is one or more of _MgO , CaO, SrO, and BaO, and _Ln2O3 is one or _more of _{La2O3 , Gd2O3} , _{and Y2O3} .

(3) A glass-ceramic product, the components of which, expressed in weight percentage, are _SiO2 : 40-60%; _Al2O3 : 20-40 _{% ; Li2O: 2-15%; Na2O: 3-20%; P2O5 + ZrO2 :} 1-15%; _K2O : 0-8% _; ZnO: 0-6%; _B2O3 : 0-6%; RO: 0-8%; TiO2: 0-5%; _{Ln2O3 :} 0-5%; and a clarifier: _0-2 %, wherein RO is one or more of _MgO , CaO, SrO, and BaO, _{and Ln2O3} is one or _more of _{La2O3 , Gd2O3} , _{and Y2O3} .

(4) A glass-ceramic product, comprising SiO ₂ , Al ₂ O ₃ , Li ₂ O and Na ₂ O, the glass-ceramic product comprising a nepheline crystal phase, and the surface stress of the glass-ceramic product being greater than 150 MPa.

(5) A glass-ceramic product, wherein the main crystal phase comprises a nepheline crystal phase, and the Vickers hardness of the glass-ceramic product is greater than 750 kgf/ ^mm2 .

(6) A glass-ceramic product, the components of which, expressed in weight percentage, include SiO ₂ : 40-60%; Al ₂ O ₃ : 20-40%; Li ₂ O: 2-15%; Na ₂ O: 3-20%, and the glass-ceramic product contains a nepheline crystal phase.

(7) A glass-ceramic product, comprising SiO ₂ , Al ₂ O ₃ , Li ₂ O and Na ₂ O, wherein the glass-ceramic product has a four-point bending strength of 700 MPa or more when the thickness is less than 1 mm.

(8) A glass-ceramic product, comprising SiO ₂ , Al ₂ O ₃ , Li ₂ O and Na ₂ O, wherein the haze of the glass-ceramic product having a thickness of 1 mm or less is 0.15% or less.

(9) A glass-ceramic product comprising a nepheline crystal phase, wherein the glass-ceramic product has a thickness of less than 1 mm and a light transmittance of 88% or more at a wavelength of 550 nm.

(10) A glass-ceramic product comprising a nepheline crystal phase, wherein the depth of the ion exchange layer of the glass-ceramic product is greater than 50 μm.

(11) The glass-ceramic product according to any one of (4) to (10), wherein the components thereof, expressed in weight percentage, include: SiO ₂ : 40-60%; and/or Al ₂ O ₃ : 20-40%; and/or Li ₂ O : 2-15%; and/or Na ₂ O : 3-20%; and/or P ₂ O ₅ +ZrO ₂ : 1-15%.

(12) The glass-ceramic product according to any one of (4) to (11), further comprising, expressed in weight percentage, _K2O : 0-8%; and/or _ZnO : 0-6%; and/or _B2O3 : 0-6%; and/or RO: 0-8%; and/or _TiO2 : 0-5%; and/or _{Ln2O3 :} 0-5%; and/or clarifier: 0-2%, wherein RO is one or more of MgO, _CaO , _SrO , and BaO, and _Ln2O3 is one or more of _La2O3 , _{Gd2O3 , and Y2O3} .

(13) The glass-ceramic product according to any one of (1) to (12), wherein the composition is expressed in weight percentage, wherein: (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 3.0 to 30.0, preferably (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 4.0 to 20.0, more preferably (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 5.0 to 15.0, and further preferably (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 6.0 to 10.0.

(14) The glass-ceramic product according to any one of (1) to (13), wherein the composition _, expressed _in weight percentage, is: _SiO2 / _Al2O3 is 1.2 to 2.8, preferably _SiO2 / _Al2O3 is 1.3 to 2.5, more preferably _SiO2 / _Al2O3 is 1.5 to 2.2, and even more preferably _{SiO2 / Al2O3} is 1.6 to 2.0 _.

(15) The glass-ceramic product according to any one of (1) to (14), wherein the composition, expressed in weight percentage, is: SiO ₂ /(Na ₂ O + B ₂ O ₃ ) is 2.0 to 15.0, preferably SiO ₂ /(Na ₂ O + B ₂ O ₃ ) is 3.0 to 10.0, more preferably SiO ₂ /(Na ₂ O + B ₂ O ₃ ) is 4.0 to 8.0, and even more preferably SiO ₂ /(Na ₂ O + B ₂ O ₃ ) is 5.0 to 7.0.

(16) The glass-ceramic product according to any one of (1) to (15), wherein the composition, expressed in weight percentage, is (Na ₂ O + Li ₂ O) / SiO ₂ in the range of 0.1 to 0.8, preferably (Na ₂ O + Li ₂ O) / SiO ₂ in the range of 0.15 to 0.7, more preferably (Na ₂ O + Li ₂ O) / SiO ₂ in the range of 0.2 to 0.6, and even more preferably (Na ₂ O + Li ₂ O) / SiO ₂ in the range of 0.25 to 0.5.

(17) The glass-ceramic product according to any one of (1) to (16), wherein the composition is expressed in weight percentage, wherein: ( _ZrO2 + ZnO)/ _Na2O is less than 2.0, preferably ( _ZrO2 + ZnO)/ _Na2O is less than 1.5, more preferably ( _ZrO2 + ZnO)/ _Na2O is 0.01 to 1.0, and even more preferably ( _ZrO2 + ZnO)/ _Na2O is 0.1 to 0.5.

(18) The glass-ceramic product according to any one of (1) to (17), wherein the composition is expressed in weight percentage, wherein: (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 0.5 to 8.0, preferably (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 0.8 to 5.0, more preferably (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 1.0 to 3.0, and further preferably (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 1.5 to 2.5.

(19) The glass-ceramic product according to any one of (1) to (18), wherein the composition is expressed in weight percentage, wherein: _K2O / _ZrO2 is greater than 0.1, preferably _K2O / _ZrO2 is 0.2-10.0, more preferably _K2O / _ZrO2 is 0.3-5.0, and even more preferably _K2O / _ZrO2 is 0.4-1.5.

(20) The glass-ceramic product according to any one of (1) to ( ₁₉ ), wherein the components are expressed in weight percentage, wherein: (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O5 is less than _1.5 , preferably (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O5 is less than 1.0, more preferably (ZnO+ _RO + _B2O3 + _{TiO2 )} / _P2O5 is less than 0.5, _and further preferably (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O5 is less than 0.2, and _the RO is one or _more of MgO, CaO, SrO, _and BaO.

(21) The glass-ceramic product according to any one of (1) to (20), wherein the components are expressed in weight percentage, wherein: SiO ₂ : 43-55%, preferably SiO ₂ : 46-53%; and/or Al ₂ O ₃ : 23-36%, preferably Al ₂ O ₃ : 25.5-32%; and/or Li ₂ O : 3-13%, preferably Li ₂ O : 5.5-11%; and/or Na ₂ O : 5-15%, preferably Na ₂ O : 6.5-12%; and/or P ₂ O ₅ + ZrO ₂ : 2-12%, preferably P ₂ O ₅ + ZrO ₂ : 4-10%; and/or K ₂ O : 0-5%, preferably K ₂ O : 0.1-3%; and/or ZnO : 0-3%, preferably ZnO : 0-1%; and/or B ₂ O ₃ : 0-3%, preferably B ₂ O ₃ : 0-1%; and/or RO: 0-5%, preferably RO: 0-2%; and/or TiO ₂ : 0-3%, preferably TiO ₂ : 0-1%; and/or Ln ₂ O ₃ : 0-3%, preferably Ln ₂ O ₃ : 0-1%; and/or clarifier: 0-1%, preferably clarifier: 0-0.5%, wherein RO is one or more of MgO, CaO, SrO, and BaO, and Ln ₂ O ₃ is one or more of La ₂ O ₃ , Gd ₂ O ₃ , and Y ₂ O ₃ .

(22) The glass-ceramic product according to any one of (1) to (21), wherein the components, expressed in weight percentage, are: ZrO ₂ : 0-6%, preferably ZrO ₂ : 0-5%, more preferably ZrO ₂ : 0.1-3%; and/or P ₂ O ₅ : 0-10%, preferably P ₂ O ₅ : 1-8%, more preferably P ₂ O ₅ : 2-6%.

(23) The glass-ceramic product according to any one of (1), ( _{2 )} , (4) to ( ₁₂ ), further comprising, expressed in weight percentage, the _following components: _Yb2O3 + _Nb2O5 + _WO3 + _Bi2O3 + _{Ta2O5 + TeO2} +GeO2 _{: 0-5} %, _preferably Yb2O3+ _Nb2O5 + _WO3 + _Bi2O3 + _{Ta2O5 + TeO2} +GeO2: _0-2 % _{, more preferably Yb2O3+Nb2O5+WO3 + Bi2O3 + Ta2O5 + TeO2 + GeO2} : _0-1 % _.

(24) The glass-ceramic product according to any one of (1) to (23), wherein its composition does not contain SrO; and/or does not contain BaO; and/or does not contain MgO; and/or does not contain CaO; and/or does not contain ZnO; and/or does not contain PbO; and/or does not contain As ₂ O ₃ ; and/or does not contain TiO ₂ ; and/or does not contain B ₂ O ₃ ; and/or does not contain Y ₂ O ₃ ; and/or does not contain La ₂ O ₃ ; and/or does not contain Gd ₂ O ₃ .

(25) The glass-ceramic product according to any one of (1) to (24), wherein the glass-ceramic product comprises a nepheline crystal phase; and/or a lithium silicate crystal phase; and/or a lithium phosphate crystal phase; and/or a tribium feldspar crystal phase; and/or a quartz crystal phase.

(26) The glass-ceramic product according to any one of (1) to (25), wherein the main crystal phase of the glass-ceramic product is the nepheline crystal phase, or the glass-ceramic product only contains the nepheline crystal phase.

(27) The glass-ceramic product according to any one of (1) to (26), wherein the weight percentage of the nepheline crystal phase in the glass-ceramic product is 10 to 80%, preferably the weight percentage of the nepheline crystal phase in the glass-ceramic product is 20 to 70%, and more preferably the weight percentage of the nepheline crystal phase in the glass-ceramic product is 30 to 60%.

(28) The glass-ceramic product according to any one of (1) to (27), wherein the ion exchange layer depth of the glass-ceramic product is greater than 50 μm, preferably greater than 60 μm, more preferably greater than 80 μm, and further preferably greater than 100 μm; and/or the Vickers hardness is greater than 750 kgf/mm ² , preferably greater than 780 kgf/mm ² , more preferably greater than 800 kgf/mm ² , and further preferably greater than 810 kgf/mm ² ; and/or the grain size is less than 80 nm, preferably less than 60 nm, more preferably less than 50 nm, and further preferably less than 40 nm; and/or the surface stress is greater than 150 MPa, preferably greater than 170 MPa, and further preferably greater than 190 MPa.

(29) The glass-ceramic product according to any one of (1) to (28), wherein the glass-ceramic product has a four-point bending strength of 700 MPa or more, preferably 750 MPa or more, and more preferably 800 MPa or more with a thickness of less than 1 mm; and/or a drop ball test height of 1100 mm or more, preferably 1300 mm or more, and more preferably 1500 mm or more; and/or a haze of 0.15% or less, preferably 0.12% or less, and more preferably 0.10% or less; and/or a light transmittance of 550 nm or more, preferably 88% or more, more preferably 89% or more, more preferably 90% or more, and further preferably 91% or more; and/or an average light |B| value of 400 to 800 nm is 1.5 or less, preferably 1.0 or less, and more preferably 0.8 or less.

(30) The glass-ceramic product according to any one of (7) to (9) and (29), wherein the thickness of the glass-ceramic product is 0.2 to 1 mm, preferably 0.3 to 0.9 mm, more preferably 0.5 to 0.8 mm, and further preferably 0.55 mm, 0.6 mm, 0.68 mm, 0.7 mm or 0.75 mm.

(31) The glass-ceramic product according to any one of (1), (2), (4) to (12), further comprising, expressed in weight percentage, the following: NiO: 0-4%; and/or Ni ₂ O ₃ : 0-4%; and/or CoO: 0-2%; and/or Co ₂ O ₃ : 0-2%; and/or Fe ₂ O ₃ : 0-7%; and/or MnO ₂ : 0-4%; and/or Er ₂ O ₃ : 0-8%; and/or Nd ₂ O ₃ : 0-8%; and/or Cu ₂ O: 0-4%; and/or Pr ₂ O ₃ : 0-8%; and/or CeO ₂ : 0-4%.

(32) A glass-ceramic, the components of which, expressed in weight percentage, include: SiO ₂ : 40-60%; Al ₂ O ₃ : 20-40%; Li ₂ O: 2-15%; Na ₂ O: 3-20%; P ₂ O ₅ +ZrO ₂ : 1-15%.

(33) The glass-ceramics according to (32), further comprising, expressed in weight percentage, _K2O : 0-8%; and/or ZnO: 0-6%; and/or _B2O3 : 0-6%; and/or _RO : 0-8%; and/or _TiO2 : 0-5%; and/or _Ln2O3 : 0-5%; and/or _clarifier : 0-2 _% , wherein RO is one or more of MgO, CaO, SrO, and BaO _{, and Ln2O3} is one or more of _La2O3 , _Gd2O3 , _{and Y2O3} .

(34) A glass-ceramic, the components of which, expressed in weight percentage, _{are SiO2} : 40-60%; _Al2O3 : 20-40% _{; Li2O: 2-15%; Na2O: 3-20%; P2O5 + ZrO2 : 1-15} %; _K2O : 0-8%; ZnO: 0-6%; _B2O3 : 0-6%; RO: 0-8%; TiO2 _: 0-5%; _Ln2O3 : 0-5%; and a clarifier: _0-2 %, wherein RO is one or more of MgO, CaO, SrO, _and BaO, _{and Ln2O3 is} one or _more of _{La2O3 , Gd2O3} , _{and Y2O3} .

(35) A glass-ceramic comprising SiO ₂ , Al ₂ O ₃ , Li ₂ O and Na ₂ O, the glass-ceramic comprising a nepheline crystal phase, and having a Vickers hardness of 650 kgf/mm ² or more.

(36) A glass-ceramic whose main crystal phase includes a nepheline crystal phase, wherein the Vickers hardness of the glass-ceramic is greater than 650 kgf/ ^mm2 .

(37) A glass-ceramic, the components of which, expressed in weight percentage, include SiO ₂ : 40-60%; Al ₂ O ₃ : 20-40%; Li ₂ O: 2-15%; and Na ₂ O: 3-20%, wherein the glass-ceramic includes a nepheline crystal phase.

(38) A glass-ceramic comprising SiO ₂ , Al ₂ O ₃ , Li ₂ O and Na ₂ O, wherein the ball-drop height of the glass-ceramic having a thickness of 1 mm or less is 1000 mm or more.

(39) A glass-ceramic comprising SiO ₂ , Al ₂ O ₃ , Li ₂ O and Na ₂ O, wherein the haze of the glass-ceramic having a thickness of 1 mm or less is 0.15% or less.

(40) A glass-ceramic comprising a nepheline crystal phase, wherein the light transmittance of the glass-ceramic having a thickness of less than 1 mm at a wavelength of 550 nm is greater than 88%.

(41) A glass-ceramic comprising SiO ₂ , Al ₂ O ₃ , Li ₂ O and Na ₂ O, wherein the weight percentage of the nepheline crystal phase in the glass-ceramic is 10 to 80%.

(42) The glass-ceramics according to any one of (35) to (41), wherein the components thereof, expressed in weight percentage, comprise: SiO ₂ : 40 to 60%; and/or Al ₂ O ₃ : 20 to 40%; and/or Li ₂ O : 2 to 15%; and/or Na ₂ O : 3 to 20%; and/or P ₂ O ₅ +ZrO ₂ : 1 to 15%.

(43) The glass-ceramics according to any one of (35) to (42), further comprising, expressed in weight percentage _{, K2O} : 0 to 8%; and/or ZnO: 0 to 6%; and/or _B2O3 : 0 to 6%; and/or RO: 0 to 8%; and/or _TiO2 : 0 to 5%; and/or _Ln2O3 : 0 to 5%; and/or _clarifier : 0 to 2%, wherein RO is one or more of _MgO , CaO, _SrO , and BaO, and _Ln2O3 is one or more of _{La2O3 , Gd2O3} , _{and Y2O3} .

(44) The glass-ceramics according to any one of (32) to (43), wherein the components are expressed in weight percentage, wherein: (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 3.0 to 30.0, preferably (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 4.0 to 20.0, more preferably (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 5.0 to 15.0, and further preferably (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 6.0 to 10.0.

(45) The glass-ceramics according to any one of (32) to (44), wherein the components are expressed in weight percentage, wherein: SiO ₂ /Al ₂ O ₃ is 1.2 to 2.8, preferably SiO ₂ /Al ₂ O ₃ is 1.3 to 2.5, more preferably SiO ₂ /Al ₂ O ₃ is 1.5 to 2.2, and further preferably SiO ₂ /Al ₂ O ₃ is 1.6 to 2.0.

(46) The glass-ceramics according to any one of (32) to (45), wherein the components are expressed in weight percentage, wherein: SiO ₂ /(Na ₂ O + B ₂ O ₃ ) is 2.0 to 15.0, preferably SiO ₂ /(Na ₂ O + B ₂ O ₃ ) is 3.0 to 10.0, more preferably SiO ₂ /(Na ₂ O + B ₂ O ₃ ) is 4.0 to 8.0, and further preferably SiO ₂ /(Na ₂ O + B ₂ O ₃ ) is 5.0 to 7.0.

(47) The glass-ceramics according to any one of (32) to (46), wherein the components are expressed in weight percentage, wherein: ( _Na2O + _Li2O )/ _SiO2 is 0.1 to 0.8, preferably ( _Na2O + _Li2O )/ _SiO2 is 0.15 to 0.7, more preferably ( _Na2O + _Li2O )/ _SiO2 is 0.2 to 0.6, and further preferably ( _Na2O + _Li2O )/ _SiO2 is 0.25 to 0.5.

(48) The glass-ceramics according to any one of (32) to (47), wherein the components are expressed in weight percentage, wherein: (ZrO ₂ + ZnO)/Na ₂ O is less than 2.0, preferably (ZrO ₂ + ZnO)/Na ₂ O is less than 1.5, more preferably (ZrO ₂ + ZnO)/Na ₂ O is 0.01 to 1.0, and further preferably (ZrO ₂ + ZnO)/Na ₂ O is 0.1 to 0.5.

(49) The glass-ceramics according to any one of (32) to (48), wherein the components are expressed in weight percentage, wherein: (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 0.5 to 8.0, preferably (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 0.8 to 5.0, more preferably (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 1.0 to 3.0, and further preferably (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 1.5 to 2.5.

(50) The glass-ceramics according to any one of (32) to (49), wherein the components are expressed in weight percentage, wherein: _K2O / _ZrO2 is greater than 0.1, preferably _K2O / _ZrO2 is 0.2 to 10.0, more preferably _K2O / _ZrO2 is 0.3 to 5.0, and even more preferably _K2O / _ZrO2 is 0.4 to 1.5.

(51) The glass-ceramics according to any one of (32) to ( ₅₀ ), wherein the components are expressed in weight percentage, wherein: (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O5 is less than _1.5 , preferably (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O5 is less than 1.0, more preferably (ZnO+RO+ _B2O3 + _{TiO2 )} / _P2O5 is less than _0.5 , and further preferably (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O5 is less than 0.2, _{and the} RO is one or _more of MgO, CaO, SrO, _and BaO.

(52) The glass-ceramics according to any one of (32) to (51), wherein the components are expressed in weight percentage, wherein: SiO ₂ : 43-55%, preferably SiO ₂ : 46-53%; and/or Al ₂ O ₃ : 23-36%, preferably Al ₂ O ₃ : 25.5-32%; and/or Li ₂ O : 3-13%, preferably Li ₂ O : 5.5-11%; and/or Na ₂ O : 5-15%, preferably Na ₂ O : 6.5-12%; and/or P ₂ O ₅ + ZrO ₂ : 2-12%, preferably P ₂ O ₅ + ZrO ₂ : 4-10%; and/or K ₂ O : 0-5%, preferably K ₂ O : 0.1-3%; and/or ZnO : 0-3%, preferably ZnO : 0-1%; and/or B ₂ O ₃ : 0-3%, preferably B ₂ O ₃ : 0-1%; and/or RO: 0-5%, preferably RO: 0-2%; and/or TiO ₂ : 0-3%, preferably TiO ₂ : 0-1%; and/or Ln ₂ O ₃ : 0-3%, preferably Ln ₂ O ₃ : 0-1%; and/or clarifier: 0-1%, preferably clarifier: 0-0.5%, wherein RO is one or more of MgO, CaO, SrO, and BaO, and Ln ₂ O ₃ is one or more of La ₂ O ₃ , Gd ₂ O ₃ , and Y ₂ O ₃ .

(53) The glass-ceramics according to any one of (32) to (52), wherein the components are expressed in weight percentage, wherein: ZrO ₂ : 0-6%, preferably ZrO ₂ : 0-5%, more preferably ZrO ₂ : 0.1-3%; and/or P ₂ O ₅ : 0-10%, preferably P ₂ O ₅ : 1-8%, more preferably P ₂ O ₅ : 2-6%.

(54) The glass-ceramics according to any one of (32), (33), (35) to (43), further comprising, expressed in weight percentage, the following components: Yb ₂ O ₃ +Nb ₂ O ₅ +WO ₃ +Bi ₂ O ₃ +Ta ₂ O ₅ +TeO ₂ +GeO ₂ : 0 to 5%, preferably Yb ₂ O ₃ +Nb ₂ O ₅ +WO ₃ +Bi ₂ O ₃ +Ta ₂ O ₅ +TeO ₂ +GeO ₂ : 0 to 2%, more preferably Yb ₂ O ₃ +Nb ₂ O ₅ +WO ₃ +Bi ₂ O ₃ +Ta ₂ O ₅ +TeO ₂ +GeO ₂ : 0 to 1%.

(55) The glass-ceramics according to any one of (32) to (54), wherein its composition does not contain SrO; and/or does not contain BaO; and/or does not contain MgO; and/or does not contain CaO; and/or does not contain ZnO; and/or does not contain PbO; and/or does not contain As ₂ O ₃ ; and/or does not contain TiO ₂ ; and/or does not contain B ₂ O ₃ ; and/or does not contain Y ₂ O ₃ ; and/or does not contain La ₂ O ₃ ; and/or does not contain Gd ₂ O ₃ .

(56) The glass-ceramics according to any one of (32) to (55), wherein the glass-ceramics comprises a nepheline crystal phase; and/or a lithium silicate crystal phase; and/or a lithium phosphate crystal phase; and/or a tribium feldspar crystal phase; and/or a quartz crystal phase.

(57) The glass-ceramics according to any one of (32) to (56), wherein the main crystal phase of the glass-ceramics is the nepheline crystal phase, or the glass-ceramics only contains the nepheline crystal phase.

(58) The glass-ceramics according to any one of (32) to (57), wherein the weight percentage of the nepheline crystal phase in the glass-ceramics is 10 to 80%, preferably the weight percentage of the nepheline crystal phase in the glass-ceramics is 20 to 70%, and more preferably the weight percentage of the nepheline crystal phase in the glass-ceramics is 30 to 60%.

(59) The glass-ceramics according to any one of (32) to (58), wherein the grain size of the glass-ceramics is less than 80 nm, preferably less than 60 nm, more preferably less than 50 nm, and further preferably less than 40 nm; and/or the Vickers hardness is greater than 650 kgf/ ^mm2 , preferably greater than 680 kgf/ ^mm2 , and more preferably greater than 700 kgf/ ^mm2 .

(60) The glass-ceramics according to any one of (32) to (59), wherein the glass-ceramics with a thickness of less than 1 mm has a body ball drop height of more than 1000 mm, preferably more than 1200 mm, and more preferably more than 1400 mm; and/or a haze of less than 0.15%, preferably less than 0.12%, and more preferably less than 0.10%; and/or a light transmittance of 550 nm wavelength of more than 88%, preferably more than 89%, more preferably more than 90%, and further preferably more than 91%; and/or an average light |B| value of 400 to 800 nm is less than 1.5, preferably less than 1.0, and more preferably less than 0.8.

(61) The glass-ceramics according to any one of (38) to (40) and (60), wherein the thickness of the glass-ceramics is 0.2 to 1 mm, preferably 0.3 to 0.9 mm, more preferably 0.5 to 0.8 mm, and further preferably 0.55 mm, 0.6 mm, 0.68 mm, 0.7 mm or 0.75 mm.

(62) The glass-ceramics according to any one of (32), (33), (35) to (43), further comprising, expressed in weight percentage, the following: NiO: 0 to 4%; and/or Ni ₂ O ₃ : 0 to 4%; and/or CoO: 0 to 2%; and/or Co ₂ O ₃ : 0 to 2%; and/or Fe ₂ O ₃ : 0 to 7%; and/or MnO ₂ : 0 to 4%; and/or Er ₂ O ₃ : 0 to 8%; and/or Nd ₂ O ₃ : 0 to 8%; and/or Cu ₂ O: 0 to 4%; and/or Pr ₂ O ₃ : 0 to 8%; and/or CeO ₂ : 0 to 4%.

(63) A matrix glass, the components of which, expressed in weight percentage, include: SiO ₂ : 40-60%; Al ₂ O ₃ : 20-40%; Li ₂ O: 2-15%; Na ₂ O: 3-20%; P ₂ O ₅ +ZrO ₂ : 1-15%.

(64) The matrix glass according to (63), further comprising, expressed in weight percentage, _K2O : 0-8%; and/or ZnO: 0-6%; and/or _B2O3 : 0-6%; and/or _RO : 0-8%; and/or _TiO2 : 0-5%; and/or _Ln2O3 : 0-5%; and/or clarifier: 0-2%, wherein RO is one or more of MgO, CaO, SrO, and BaO _{, and Ln2O3} is one or _more of _{La2O3 , Gd2O3} , _{and Y2O3} .

(65) A matrix glass, the components of which, expressed in weight percentage, _{are SiO2} : 40-60%; _Al2O3 : 20-40% _{; Li2O: 2-15%; Na2O: 3-20%; P2O5 + ZrO2 : 1-15} %; _K2O : 0-8%; ZnO: 0-6%; _B2O3 : 0-6%; RO: 0-8%; _TiO2 : 0-5%; _Ln2O3 : 0-5%; and clarifier: _0-2 %, wherein RO is one or more of MgO, CaO, SrO, and BaO _{, and Ln2O3 is one} or _more of _La2O3 , _{Gd2O3 , and Y2O3} .

(66) The matrix glass according to any one of (63) to (65), wherein the composition is expressed in weight percentage, wherein: (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 3.0 to 30.0, preferably (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 4.0 to 20.0, more preferably (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 5.0 to 15.0, and further preferably (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 6.0 to 10.0.

(67) The matrix glass according to any one of (63) to (66), wherein the composition _{, expressed in weight percentage, is SiO2/Al2O3 in the} range of 1.2 to _2.8 , preferably _SiO2 / _Al2O3 in the range of 1.3 to 2.5, more preferably _SiO2 / _Al2O3 in the range of 1.5 to 2.2 _, and even more preferably _{SiO2 / Al2O3} in the range of 1.6 to 2.0.

(68) The matrix glass according to any one of (63) to ( ₆₇ ), wherein the composition is expressed in weight percentage, wherein: _SiO2 /( _Na2O + _B2O3 ) is 2.0 to 15.0, preferably _SiO2 /( _Na2O + _B2O3 ) is 3.0 to _10.0 , more preferably _SiO2 /( _{Na2O +B2O3 )} is 4.0 to 8.0, and further preferably _SiO2 /( _Na2O + _B2O3 ) is 5.0 to _7.0 .

(69) The matrix glass according to any one of (63) to (68), wherein the composition is expressed in weight percentage, wherein: ( _Na2O + _Li2O )/ _SiO2 is 0.1 to 0.8, preferably ( _Na2O + _Li2O )/ _SiO2 is 0.15 to 0.7, more preferably ( _Na2O + _Li2O )/ _SiO2 is 0.2 to 0.6, and further preferably ( _Na2O + _Li2O )/ _SiO2 is 0.25 to 0.5.

(70) The matrix glass according to any one of (63) to (69), wherein the composition is expressed in weight percentage, wherein: ( _ZrO2 + ZnO)/ _Na2O is less than 2.0, preferably ( _ZrO2 + ZnO)/ _Na2O is less than 1.5, more preferably ( _ZrO2 + ZnO)/ _Na2O is 0.01 to 1.0, and even more preferably ( _ZrO2 + ZnO)/ _Na2O is 0.1 to 0.5.

(71) The matrix glass according to any one of ( ₆₃ ) to (70), wherein the composition is expressed in weight percentage, wherein: ( _P2O5 + _Na2O )/ _Li2O is _0.5 to 8.0, preferably ( _P2O5 + _Na2O )/ _Li2O is 0.8 to 5.0, more preferably ( _P2O5 + _Na2O )/ _Li2O is _1.0 to 3.0, and further preferably ( _P2O5 + _Na2O )/ _Li2O is _1.5 to 2.5.

(72) The matrix glass according to any one of (63) to (71), wherein the composition is expressed in weight percentage, wherein: _K2O / _ZrO2 is greater than 0.1, preferably _K2O / _ZrO2 is 0.2 to 10.0, more preferably _K2O / _ZrO2 is 0.3 to 5.0, and even more preferably _K2O / _ZrO2 is 0.4 to 1.5.

(73) The matrix glass according to any one of (63) to ( ₇₂ ), wherein the components are expressed in weight percentage, wherein: (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O5 is less than _1.5 , preferably (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O5 is less than _1.0 , more preferably (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O5 is less than _0.5 , _and further preferably (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O5 is less than 0.2, _and the RO is one or _more of MgO, CaO, SrO, _and BaO.

(74) The matrix glass according to any one of (63) to (73), wherein the components thereof are expressed in weight percentage, wherein: SiO ₂ : 43-55%, preferably SiO ₂ : 46-53%; and/or Al ₂ O ₃ : 23-36%, preferably Al ₂ O ₃ : 25.5-32%; and/or Li ₂ O : 3-13%, preferably Li ₂ O : 5.5-11%; and/or Na ₂ O : 5-15%, preferably Na ₂ O : 6.5-12%; and/or P ₂ O ₅ + ZrO ₂ : 2-12%, preferably P ₂ O ₅ + ZrO ₂ : 4-10%; and/or K ₂ O : 0-5%, preferably K ₂ O : 0.1-3%; and/or ZnO : 0-3%, preferably ZnO : 0-1%; and/or B ₂ O ₃ : 0-3%, preferably B ₂ O ₃ : 0-1%; and/or RO: 0-5%, preferably RO: 0-2%; and/or TiO ₂ : 0-3%, preferably TiO ₂ : 0-1%; and/or Ln ₂ O ₃ : 0-3%, preferably Ln ₂ O ₃ : 0-1%; and/or clarifier: 0-1%, preferably clarifier: 0-0.5%, wherein RO is one or more of MgO, CaO, SrO, and BaO, and Ln ₂ O ₃ is one or more of La ₂ O ₃ , Gd ₂ O ₃ , and Y ₂ O ₃ .

(75) The matrix glass according to any one of (63) to (74), wherein the components thereof are expressed in weight percentage, wherein: ZrO ₂ : 0-6%, preferably ZrO ₂ : 0-5%, more preferably ZrO ₂ : 0.1-3%; and/or P ₂ O ₅ : 0-10%, preferably P ₂ O ₅ : 1-8%, more preferably P ₂ O ₅ : 2-6%.

(76) The base glass according to (63) or (64), wherein the composition _, expressed in weight percentage, further comprises: _{Yb2O3 + Nb2O5 + WO3 + Bi2O3} +Ta2O5+TeO2+ _GeO2 : _{0-5 %} , _preferably Yb2O3+ _{Nb2O5 + WO3} + _{Bi2O3 + Ta2O5 + TeO2} +GeO2 _{: 0-2} %, _{more preferably Yb2O3} + _Nb2O5 + _{WO3 + Bi2O3} + _Ta2O5 + _TeO2 + _GeO2 : _0-1 %.

(77) The base glass according to any one of (63) to (65), wherein its composition does not contain SrO; and/or does not contain BaO; and/or does not contain MgO; and/or does not contain CaO; and/or does not contain ZnO; and/or does not contain PbO; and/or does not contain As ₂ O ₃ ; and/or does not contain TiO ₂ ; and/or does not contain B ₂ O ₃ ; and/or does not contain Y ₂ O ₃ ; and/or does not contain La ₂ O ₃ ; and/or does not contain Gd ₂ O ₃ .

(78) The matrix glass according to (63) or (64), wherein the components, expressed in weight percentage, further comprise: NiO: 0-4%; and/or Ni ₂ O ₃ : 0-4%; and/or CoO: 0-2%; and/or Co ₂ O ₃ : 0-2%; and/or Fe ₂ O ₃ : 0-7%; and/or MnO ₂ : 0-4%; and/or Er ₂ O ₃ : 0-8%; and/or Nd ₂ O ₃ : 0-8%; and/or Cu ₂ O: 0-4%; and/or Pr ₂ O ₃ : 0-8%; and/or CeO ₂ : 0-4%.

(79) A glass-ceramic formed body comprising the glass-ceramic described in any one of (32) to (62).

(80) A glass cover comprising the microcrystalline glass product described in any one of (1) to (31), and/or the microcrystalline glass described in any one of (32) to (62), and/or the base glass described in any one of (63) to (78), and/or the microcrystalline glass formed body described in (79).

(81) A glass component comprising the glass-ceramic product described in any one of (1) to (31), and/or the glass-ceramic product described in any one of (32) to (62), and/or the base glass described in any one of (63) to (78), and/or the glass-ceramic formed body described in (79).

(82) A display device comprising the microcrystalline glass product described in any one of (1) to (31), and/or the microcrystalline glass described in any one of (32) to (62), and/or the base glass described in any one of (63) to (78), and/or the microcrystalline glass formed body described in (79), and/or the glass cover described in (80), and/or the glass component described in (81).

(83) An electronic device comprising the microcrystalline glass product described in any one of (1) to (31), and/or the microcrystalline glass described in any one of (32) to (62), and/or the base glass described in any one of (63) to (78), and/or the microcrystalline glass formed body described in (79), and/or the glass cover described in (80), and/or the glass component described in (81).

(84) A method for manufacturing a glass-ceramic product according to any one of (1) to (31), the method comprising the following steps: forming a base glass, subjecting the base glass to a crystallization process to form a glass-ceramic, and then subjecting the glass-ceramic to a chemical strengthening process to form a glass-ceramic product.

(85) According to the manufacturing method of microcrystalline glass products described in (84), the crystallization process includes the following steps: heating to a specified crystallization treatment temperature, maintaining the temperature for a certain period of time after reaching the crystallization treatment temperature, and then cooling down, the crystallization treatment temperature is 580-750°C, preferably 600-700°C, and the holding time at the crystallization treatment temperature is 0-8 hours, preferably 1-6 hours.

(86) According to the method for manufacturing a microcrystalline glass product described in (84), the crystallization process includes the following steps: performing a nucleation process at a first temperature, and then performing a crystal growth process at a second temperature higher than the nucleation process temperature.

(87) According to the method for manufacturing a microcrystalline glass product described in (86), the crystallization process comprises the following steps: the first temperature is 500-620°C, and the second temperature is 620-750°C; the holding time at the first temperature is 0-24 hours, preferably 2-15 hours; the holding time at the second temperature is 0-10 hours, preferably 0.5-6 hours.

(88) According to any one of the methods for manufacturing glass-ceramics products described in (84) to (87), the chemical strengthening process comprises: immersing the glass-ceramics in a salt bath of molten Na salt at a temperature of 350 to 470°C for 1 to 36 hours, preferably in a temperature range of 380 to 460°C, and preferably in a time range of 2 to 10 hours; and/or immersing the glass-ceramics in a salt bath of molten K salt at a temperature of 360 to 450°C for 1 to 36 hours, preferably in a time range of 1 to 10 hours; and/or immersing the glass-ceramics in a mixed salt bath of molten K salt and Na salt at a temperature of 360 to 450°C for 1 to 36 hours, preferably in a time range of 2 to 24 hours.

(89) A method for manufacturing glass-ceramics according to any one of (32) to (62), comprising the steps of forming a base glass and then subjecting the base glass to a crystallization process to form glass-ceramics.

(90) According to the method for manufacturing microcrystalline glass described in (89), the crystallization process includes the following steps: heating to a specified crystallization treatment temperature, maintaining the temperature for a certain period of time after reaching the crystallization treatment temperature, and then cooling down, the crystallization treatment temperature is 580-750°C, preferably 600-700°C, and the holding time at the crystallization treatment temperature is 0-8 hours, preferably 1-6 hours.

(91) According to the method for manufacturing microcrystalline glass described in (89), the crystallization process includes the following steps: performing a nucleation process at a first temperature, and then performing a crystal growth process at a second temperature higher than the nucleation process temperature.

(92) According to the method for manufacturing microcrystalline glass described in (91), the crystallization process includes the following steps: the first temperature is 500-620°C, and the second temperature is 620-750°C; the holding time at the first temperature is 0-24 hours, preferably 2-15 hours; the holding time at the second temperature is 0-10 hours, preferably 0.5-6 hours.

(93) A method for manufacturing a glass-ceramic molded body according to (79), the method comprising grinding or polishing the glass-ceramic to form a glass-ceramic molded body, or subjecting a base glass or glass-ceramic to a hot bending process or a pressing process at a certain temperature to form a glass-ceramic molded body.

(94) The method for manufacturing a glass-ceramic molded body according to (79) comprises the following steps: subjecting the base glass to a primary crystallization heat treatment process, including heating, heat preservation for nucleation, heating, heat preservation for crystallization, and cooling to room temperature to form pre-crystallized glass; and subjecting the pre-crystallized glass to heat processing and molding to obtain a glass-ceramic molded body.

(95) The method for manufacturing a glass-ceramic formed body according to (79), comprising the following steps:

1) Heating and preheating: Place the base glass or pre-crystallized glass or microcrystalline glass in the mold. The mold passes through each heating station in the hot bending machine in turn and stays at each heating station for a certain period of time to keep warm. The temperature in the preheating zone is 400-800℃, the pressure is 0.01-0.05MPa, and the time is 40-200s;

2) Pressurized molding: After preheating, the mold is transferred to the molding station. The hot bending machine applies a certain pressure to the mold. The pressure range is 0.1-0.8Mpa, the molding station temperature range is 650-850℃, and the molding time range is 40-200s;

3) Pressure-maintaining cooling: The mold is transferred to the cooling station for cooling step by step. The cooling temperature range is 750-500°C, the pressure is 0.01-0.05Mpa, and the time is 40-200s.

The beneficial effect of the present invention is that through reasonable component design, the microcrystalline glass or microcrystalline glass products obtained by the present invention have excellent mechanical properties and meet the application in the fields of display equipment or electronic equipment.

The following is a detailed description of the implementation of the optical glass of the present invention, but the present invention is not limited to the following implementation and can be implemented with appropriate changes within the scope of the purpose of the present invention. In addition, although there are appropriate omissions in the description of repeated parts, the main purpose of the invention will not be limited thereby. In the following content, the optical glass of the present invention is sometimes referred to as glass. The microcrystalline glass and microcrystalline glass products of the present invention are materials having a crystalline phase (sometimes also referred to as a crystal) and a glass phase, which are different from amorphous solids. The crystalline phase of microcrystalline glass and microcrystalline glass products can be identified by the peak angle appearing in the X-ray diffraction pattern of X-ray diffraction analysis and/or measured by TEMEDX.

After repeated experiments and studies, the inventors of the present invention have obtained the microcrystalline glass or microcrystalline glass products of the present invention by regulating the content and content ratio of the specific components constituting microcrystalline glass and microcrystalline glass products to specific values and precipitating specific crystalline phases.

The following is an explanation of the scope of each component (ingredient) of the base glass, glass-ceramic, and glass-ceramic products of the present invention. In this specification, unless otherwise specified, the content of each component is expressed in terms of weight percentage (wt%) relative to the total amount of the base glass, glass-ceramic, or glass-ceramic product material converted into an oxide composition. Here, the "composition converted into oxides" refers to the case where oxides, complex salts, hydroxides, etc. used as raw materials for the base glass, glass-ceramic, or glass-ceramic product components of the present invention decompose and transform into oxides when melted, and the total weight of the oxide material is taken as 100%. In addition, in this manual, when the word "glass" is used, it refers to the base glass before crystallization (i.e., crystallization process treatment). The base glass after crystallization (i.e., crystallization process treatment) is called microcrystalline glass. Microcrystalline glass products refer to products obtained after chemical strengthening of microcrystalline glass.

Unless otherwise indicated in specific circumstances, the numerical ranges listed herein include upper and lower limits, "above" and "below" include the endpoints, as well as all integers and fractions within the range, and are not limited to the specific values listed when defining the range. The term "about" used herein means that the formula, parameters and other quantities and features are not and do not need to be exact, and may be approximate and/or larger or lower if necessary, reflecting tolerances, conversion factors and measurement errors, etc. "And/or" as used herein is inclusive, for example, "A; and/or B" means only A, or only B, or both A and B.

In some embodiments, the crystal phase of the glass-ceramics or glass-ceramics products of the present invention includes a nepheline crystal phase (including lithium nepheline and/or sodium nepheline), specifically, includes lithium nepheline, or includes sodium nepheline, or includes lithium nepheline and sodium nepheline at the same time. The glass-ceramics of the present invention may also have other crystal phases besides the nepheline crystal phase, such as a lithium silicate crystal phase (one or both of lithium monosilicate and lithium disilicate); and/or a lithium phosphate crystal phase; and/or a triboephtalite crystal phase; and/or a quartz crystal phase.

In some embodiments of the present invention, the crystal phase in the microcrystalline glass or microcrystalline glass products only contains nepheline crystal phase (one or both of lithium nepheline and sodium nepheline).

In some embodiments, when the microcrystalline glass or microcrystalline glass products contain nepheline crystal phase and other crystal phases, the main crystal phase of the microcrystalline glass or microcrystalline glass products is the nepheline crystal phase, that is, the nepheline crystal phase has a higher weight percentage than other crystal phases.

In some embodiments, the weight percentage of the nepheline crystal phase in the microcrystalline glass or microcrystalline glass products is 10-80%, preferably the weight percentage of the nepheline crystal phase in the microcrystalline glass or microcrystalline glass products is 20-70%, and more preferably the weight percentage of the nepheline crystal phase in the microcrystalline glass or microcrystalline glass products is 30-60%. In some embodiments, the nepheline crystal phase accounts for about 10%, 11%, 12%, 13%, 14%, 15%, 16%, 17%, 18%, 19%, 20%, 21%, 22%, 23%, 24%, 25%, 26%, 27%, 28%, 29%, 30%, 31%, 32%, 33%, 34%, 35%, 36%, 37%, 38%, 39%, 40%, 41%, 42%, 43%, 44%, 45%, 46%, 47%, 48%, 49%, 50%, 51%, 52%, 53%, 54%, 55%, 56%, 57%, 58%, 59%, 60%, 61%, 62%, 63%, 64%, 65%, 66%, 67%, 68%, 69%, 70%, 71%, 72%, 73%, 74%, 75%, 76%, 77%, 78%, 79%, 80% by weight of the glass-ceramic or glass-ceramic product.

_SiO2 is a basic component of the matrix glass, glass-ceramics and glass-ceramics products of the present invention, and can be used to stabilize the network structure of glass and glass-ceramics. It is one of the components that form the nepheline crystal phase after crystallization. If the content of _SiO2 is below 40%, the crystals formed in the glass-ceramics will become less and the crystals will easily become coarser, affecting the haze of the glass-ceramics and glass-ceramics products, as well as the performance of the glass-ceramics products such as the drop ball test height. Therefore, the lower limit of the _SiO2 content is 40%, the preferred lower limit is 43%, and the more preferred lower limit is 46%. If the content of _SiO2 exceeds 60%, the glass melting temperature is high, clarification is difficult, and it is not easy to form, which affects the consistency of the glass, and affects the hot bending of the glass and glass-ceramics, and is unfavorable to the surface stress and ion exchange layer depth of the glass-ceramics products. Therefore, the upper limit of _SiO2 content is 60%, preferably 55%, and more preferably 53%. In some embodiments, about 40%, 40.5%, 41%, 41.5%, 42%, 42.5%, 43%, 43.5%, 44%, 44.5%, 45%, 45.5%, 46%, 46.5%, 47%, 47.5%, 48%, 48.5%, 49%, 49.5%, 50%, 50.5%, 51%, 51.5%, 52%, 52.5%, 53%, 53.5%, 54%, 54.5%, 55%, 55.5%, 56%, 56.5%, 57%, 57.5%, 58%, 58.5%, 59%, 59.5%, 60% _{SiO2 may} be included.

_Al2O3 is _a component that forms a glass network structure. It is an important component that helps stabilize glass molding and improve chemical stability. It can also improve the mechanical properties of glass and increase the depth of the ion exchange layer and surface stress of microcrystalline glass products. However, if _{the Al2O3} content is too high, the glass's solubility and resistance to devitrification will decrease, and the crystals will easily increase during crystallization, reducing the strength of microcrystalline glass and microcrystalline glass products. Therefore, the content _{of Al2O3} in the present invention is 20-40%, preferably 23-36%, and more preferably 25.5-32%. In some embodiments, about 20%, 20.5%, 21%, 21.5%, 22%, 22.5%, 23%, 23.5%, 24%, 24.5%, 25%, 25.5%, 26%, 26.5%, 27%, 27.5%, 28%, 28.5%, 29%, 29.5%, 30%, 30.5%, 31%, 31.5%, 32%, 32.5%, 33%, 33.5%, 34%, 34.5%, 35%, 35.5%, 36%, 36.5%, 37%, 37.5%, 38%, 38.5%, 39%, 39.5%, 40% _Al2O3 may be _included .

In some embodiments, the ratio of SiO ₂ to Al ₂ O ₃ , SiO ₂ /Al ₂ O _3, is controlled within the range of 1.2 to 2.8, which can improve the four-point bending strength of microcrystalline glass and microcrystalline glass products, and improve the light transmittance of microcrystalline glass and microcrystalline glass products. Therefore, SiO ₂ /Al ₂ O ₃ is preferably 1.2 to 2.8, and SiO ₂ /Al ₂ O ₃ is more preferably 1.3 to 2.5. Furthermore, by controlling SiO ₂ /Al ₂ O ₃ within the range of 1.5 to 2.2, the |B| value of microcrystalline glass and microcrystalline glass products can be further reduced, and the surface stress of microcrystalline glass products can be improved. Therefore, SiO ₂ /Al ₂ O ₃ is further preferably 1.5 to 2.2, and SiO ₂ /Al ₂ O ₃ is further preferably 1.6 to 2.0. In some embodiments, the value of _SiO2 / _Al2O3 may be 1.2, 1.25, 1.3, 1.35, 1.4, 1.45, 1.5, 1.55, 1.6, 1.65, 1.7, 1.75, 1.8, 1.85, 1.9, 1.95, 2.0, 2.05, 2.1, 2.15, 2.2, 2.25, 2.3, 2.35, 2.4, 2.45, 2.5, 2.55, 2.6, 2.65, 2.7, 2.75 _, 2.8.

_Li2O can promote the melting of glass, reduce the melting temperature of glass, form lithium nepheline crystal phase after crystallization, and is also the main component that replaces sodium and potassium ions in the chemical strengthening process. It can increase the surface stress of microcrystalline glass products, help to improve the drop ball test height of microcrystalline glass products, and increase the dielectric constant of microcrystalline glass and microcrystalline glass products. On the other hand, if _Li2O is contained too much, it is easy to reduce the chemical stability of glass, and deteriorate the light transmittance of microcrystalline glass and microcrystalline glass products. Therefore, the content of _Li2O in the present invention is 2-15%, preferably 3-13%, and more preferably 5.5-11%. In some embodiments, about 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5%, 5.5%, 6%, 6.5%, 7%, 7.5%, 8%, 8.5%, 9%, 9.5%, 10%, 10.5%, 11%, 11.5%, 12%, 12.5%, 13%, 13.5%, 14%, 14.5%, 15% _Li2O may be included.

_Na2O can participate in crystallization to form sodium nepheline crystal phase after crystallization, and can also participate in chemical strengthening and improve the solubility of glass. On the other hand, if the content of _Na2O is too high, it is easy to cause the precipitated grains to increase or the type of precipitated crystal phase to change during the crystallization process. Therefore, the content of _Na2O in the present invention is 3-20%, preferably 5-15%, and more preferably 6.5-12%. In some embodiments, about 3%, 3.5%, 4%, 4.5%, 5%, 5.5%, 6%, 6.5%, 7%, 7.5%, 8%, 8.5%, 9%, 9.5%, 10%, 10.5%, 11%, 11.5%, 12%, 12.5%, 13%, 13.5%, 14%, 14.5%, 15%, 15.5%, 16%, 16.5%, 17%, 17.5%, 18%, 18.5%, 19%, 19.5%, 20% _Na2O may be included.

In some embodiments, the ratio of the total content of Na ₂ O and Li ₂ O (Na ₂ O+Li ₂ O) to the content of SiO ₂ ((Na ₂ O+Li ₂ O)/SiO ₂₎ is controlled within the range of 0.1 to 0.8, which is beneficial for the microcrystalline glass and microcrystalline glass products to obtain the desired crystalline phase content, while refining the grains and improving the hardness of the microcrystalline glass and microcrystalline glass products. Therefore, it is preferred that (Na ₂ O+Li ₂ O)/SiO ₂ is 0.1 to 0.8, and it is more preferred that (Na ₂ O+Li ₂ O)/SiO ₂ is 0.15 to 0.7. Furthermore, by controlling (Na ₂ O+Li ₂ O)/SiO ₂ within the range of 0.2 to 0.6, the light transmittance of the microcrystalline glass and microcrystalline glass products can be further improved, and the haze can be optimized. Therefore, it is further preferred that ( _Na2O + _Li2O )/ _SiO2 is 0.2 to 0.6, and it is further preferred that ( _Na2O + _Li2O )/ _SiO2 is 0.25 to 0.5. In some embodiments, the value of ( _Na2O + _Li2O )/ _SiO2 may be 0.1, 0.15, 0.2, 0.25, 0.3, 0.35, 0.4, 0.45, 0.5, 0.55, 0.6, 0.65, 0.7, 0.75, or 0.8.

_K2O is an optional component that helps improve the low temperature melting property and formability of glass, but if _K2O is contained too much, it is easy to reduce the chemical stability of glass. Therefore, the content of _K2O is 0-8%, preferably 0-5%, and more preferably 0.1-3%. In some embodiments, about 0%, more than 0%, 0.01%, 0.05%, 0.1%, 0.5%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5%, 5.5%, 6%, 6.5%, 7%, 7.5%, 8% of _{K2O may} be contained.

_P2O5 can form crystal nuclei in glass, promote uniform crystal growth, and help improve the low-temperature melting property of glass; however _{, if P2O5 is} contained in excessive amounts, it is easy to reduce the resistance to devitrification and glass phase separation, and the mechanical properties of microcrystalline glass and microcrystalline glass products tend to deteriorate. Therefore, the content _{of P2O5 in} the present invention is 0-10%, preferably 1-8%, and more preferably 2-6%. In some embodiments _, about 0%, greater than 0%, 0.01%, 0.05%, 0.1%, 0.5%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5%, 5.5%, 6%, 6.5%, 7%, 7.5%, 8%, 8.5%, 9%, 9.5%, 10% of _{P2O5 may be included} .

In some embodiments, the ratio of the total content of _Al2O3 and _{Na2O (Al2O3 + Na2O ) to the content of P2O5 ( ( Al2O3} + _Na2O )/ _{P2O5 )} is controlled within the range of 3.0 to 30.0, which is beneficial for the microcrystalline glass and microcrystalline glass products to obtain the desired crystalline phase content, and improve the Vickers hardness of the _{microcrystalline} glass and _{microcrystalline} glass products, and increase the height of the drop ball test. Therefore, it is preferred that ( _Al2O3 + _Na2O )/ _P2O5 is _3.0 to 30.0, and _more preferably _{( Al2O3} + _Na2O )/ _P2O5 is 4.0 to 20.0. Furthermore, by controlling (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ in the range of 5.0 to 15.0, the four-point bending strength of the microcrystalline glass and the microcrystalline glass products can be further optimized, and the ion exchange layer depth of the microcrystalline glass products can be increased. Therefore, it is further preferred that (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 5.0 to 15.0, and it is further preferred that (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 6.0 to 10.0. In some embodiments, (Al ₂ O ₃ +Na ₂ O)/P ₂ O The values of ₅ can be 3.0, 3.5, 4.0, 4.5, 5.0, 5.5, 6.0, 6.5, 7.0, 7.5, 8.0, 8.5, 9.0, 9.5, 10.0, 10.5, 11.0, 11.5, 12.0, 12.5, 13.0, 13.5, 14.0, 14.5, 15.0, 15.5, 16.0, 16.5, 17 .0, 17.5, 18.0, 18.5, 19.0, 19.5, 20.0, 20.5, 21.0, 21.5, 22.0, 22.5, 23.0, 23.5, 24.0, 24.5, 25.0, 25.5, 26.0, 26.5, 27.0, 27.5, 28.0, 28.5, 29.0, 29.5, 30.0.

In some embodiments, the ratio of the total content of _{P2O5 and Na2O (P2O5 + Na2O} ) to the content of _Li2O (( _P2O5 + _Na2O )/ _Li2O ) is controlled within the range of _0.5 to 8.0, which is beneficial to increasing the drop ball test height of the _{microcrystalline} glass and microcrystalline glass products and increasing the ion exchange layer depth of the microcrystalline glass products. Therefore, it is preferred that ( _P2O5 + _Na2O )/ _Li2O is 0.5 to 8.0, and it is more preferred that ( _P2O5 + _Na2O )/ _{Li2O is 0.8 to 5.0. Furthermore, by controlling (P2O5 +Na2O)/Li2O within the range} of 1.0 to 3.0, the hardness and | _{B |} value of the microcrystalline glass and microcrystalline glass products can be further optimized. Therefore, (P ₂ O ₅ +Na ₂ O)/Li ₂ O is more preferably 1.0 to 3.0, and even more preferably (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 1.5 to 2.5. In some embodiments, the value of ( _P2O5 + _Na2O )/ _Li2O may be 0.5, 0.6, 0.7, 0.8, 0.9, 1.0, 1.1, _1.2 , 1.3, 1.4, 1.5, 1.6, 1.7, 1.8, 1.9, 2.0, 2.1, 2.2, 2.3, 2.4, 2.5, 2.6, 2.7, 2.8, 2.9, 3.0, 3.1, 3.2, 3.3, 3.4, 3.5, 3.6, 3.7, 3.8, 3.9, 4.0, 4.5, 5.0, 5.5, 6.0, 6.5, 7.0, 7.5, 8.0.

ZrO ₂ has the function of crystallization and precipitation to form crystal nuclei, and at the same time helps to improve the chemical stability of glass. Studies have found that ZrO ₂ can also improve the stability of glass by significantly reducing glass devitrification and lowering the liquidus temperature during the melting process; but if too much ZrO ₂ is contained, the devitrification resistance of the glass is easily reduced, and the difficulty of controlling the glass crystallization process increases. Therefore, the content of ZrO ₂ is 0-6%, preferably 0-5%, and more preferably 0.1-3%. In some embodiments, about 0%, greater than 0%, 0.01%, 0.05%, 0.1%, 0.5%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5%, 5.5%, 6% ZrO ₂ may be included.

In some embodiments, controlling the ratio of K ₂ O content to ZrO ₂ content, K ₂ O/ZrO ₂ , to be above 0.1 is beneficial to grain refinement and reducing the haze and grain size of microcrystalline glass and microcrystalline glass products. Therefore, it is preferred that K ₂ O/ZrO ₂ is above 0.1, and it is more preferred that K ₂ O/ZrO ₂ is 0.2-10.0. Furthermore, controlling K ₂ O/ZrO ₂ within the range of 0.3-5.0 can further optimize the light transmittance of microcrystalline glass and microcrystalline glass products and prevent the depth of the ion exchange layer of microcrystalline glass products from deteriorating. Therefore, it is further preferred that K ₂ O/ZrO ₂ is 0.3-5.0, and it is further preferred that K ₂ O/ZrO ₂ is 0.4-1.5. In some embodiments, K ₂ O/ZrO The value of ₂ can be 0.1, 0.15, 0.2, 0.25, 0.3, 0.35, 0.4, 0.45, 0.5, 0.55, 0.6, 0.65, 0.7, 0.75, 0.8, 0.85, 0.9, 0.95, 1.0, 1.05, 1.1, 1.15, 1.2, 1.25, 1.3, 1.35, 1.4, 1.45, 1.5, 1.55, 1.6, 1.65, 1.7, 1.75, 1.8, 1.85, 1.9, 1.95, 2.0, 2.1, 2.2, 2.3, 2.4, 2.5, 2.6, 2.7, 2.8, 2.9, 3.0, 3.1, 3.2, 3.3, 3.4, 3.5, 3.6, 3.7, 3.8, 3.9, 4.0, 4.1, 4.2, 4.3, 4.4, 4.5, 4.6, 4.7, 4.8, 4.9, 5.0, 5.5, 6.0, 6.5, 7.0, 7.5, 8.0, 8.5, 9.0, 9.5, 10.0.

In some embodiments, the combined content of _P2O5 and _{ZrO2 , P2O5} + _{ZrO2, is} controlled within the range of 1-15%, which is beneficial to grain refinement, reducing the grain size of microcrystalline glass and microcrystalline glass products, while reducing the |B _| value of _{microcrystalline glass and microcrystalline glass products, and improving the light transmittance of microcrystalline glass and microcrystalline glass products. Therefore, it is preferred that P2O5 + ZrO2} is 1-15%, more preferably _P2O5 + _ZrO2 is 2-12%, _and further preferably _P2O5 + _ZrO2 is 4-10%. In some embodiments, _P2O5 + _ZrO2 may be 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5%, 5.5%, 6%, 6.5%, ₇ %, 7.5%, 8%, 8.5%, 9%, 9.5%, 10%, 10.5%, 11%, 11.5%, 12%, 12.5%, 13%, 13.5%, 14%, 14.5%, 15%.

ZnO can improve the melting performance of glass, improve the chemical stability of glass, refine grains during crystallization, control the upper limit of ZnO content below 6%, and inhibit the reduction of devitrification resistance. Therefore, the ZnO content is 0-6%, preferably 0-3%, and more preferably 0-1%. In some embodiments, about 0%, greater than 0%, 0.01%, 0.05%, 0.1%, 0.5%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5%, 5.5%, 6% ZnO may be included.

In some embodiments, the ratio of the total content of _ZrO2 and ZnO _ZrO2 + ZnO to the content of _Na2O ( _ZrO2 + ZnO) / _Na2O is controlled to be below 2.0, which is beneficial to reducing the haze and grain size of the microcrystalline glass and microcrystalline glass products, and increasing the drop ball test height of the microcrystalline glass and microcrystalline glass products. Therefore, it is preferred that ( _ZrO2 + ZnO) / _Na2O is below 2.0, more preferably ( _ZrO2 + ZnO) / _Na2O is below 1.5, further preferably ( _ZrO2 + ZnO) / _Na2O is 0.01 to 1.0, and further preferably ( _ZrO2 + ZnO) / _Na2O is 0.1 to 0.5. In some embodiments, the value of ( _ZrO2 + ZnO)/ _Na2O can be 0, greater than 0, 0.01, 0.05, 0.1, 0.15, 0.2, 0.25, 0.3, 0.35, 0.4, 0.45, 0.5, 0.55, 0.6, 0.65, 0.7, 0.75, 0.8, 0.85, 0.9, 0.95, 1.0, 1.05, 1.1, 1.15, 1.2, 1.25, 1.3, 1.35, 1.4, 1.45, 1.5, 1.55, 1.6, 1.65, 1.7, 1.75, 1.8, 1.85, 1.9, 1.95, 2.0.

_B2O3 can improve the network structure of glass and adjust the chemical strengthening properties of microcrystalline glass _. If its content is too much, it is not conducive to glass molding, _and it is easy to crystallize during molding, and the chemical stability is reduced. Therefore, the content of _B2O3 is 0-6%, preferably 0-3%, and more preferably 0-1%. In some embodiments, about 0%, greater than 0%, 0.01%, 0.05%, 0.1%, 0.5%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5%, 5.5%, 6% _B2O3 may be _included .

In some embodiments, the ratio _of SiO ₂ to the total content of Na ₂ O and B ₂ O ₃ (Na ₂ O + B ₂ O ₃ ) is controlled within the range of 2.0 to 15.0, which is beneficial to increasing the ion exchange layer depth of the microcrystalline glass product and improving _the four-point _bending strength _of the microcrystalline glass and the microcrystalline glass product. Therefore, SiO ₂ / (Na ₂ O + B ₂ O ₃ ) is preferably 2.0 to 15.0, and SiO ₂ / (Na ₂ O + B ₂ O ₃ ) is more preferably 3.0 to 10.0. Furthermore, by controlling SiO ₂ /(Na ₂ O+B ₂ O ₃ ) within the range of 4.0 to 8.0, the surface stress of the glass-ceramic products can be further optimized, and the drop ball test height of the glass-ceramic and the glass-ceramic products can be increased. Therefore, SiO ₂ /(Na ₂ O+B ₂ O ₃ ) is further preferably 4.0 to 8.0, and SiO ₂ /(Na ₂ O+B ₂ O ₃ ) is further preferably 5.0 to 7.0. In some embodiments, the value of _SiO2 /( _Na2O + _B2O3 ) may be 2.0, 2.5, 3.0, 3.5, 4.0, 4.5, 5.0, 5.5, 6.0, 6.5, 7.0, 7.5, 8.0, 8.5, 9.0, 9.5, 10.0, 10.5, 11.0, 11.5, 12.0, 12.5, 13.0, 13.5, 14.0 _, 14.5, 15.0.

Alkaline earth metal oxides RO (RO is one or more of MgO, CaO, SrO, BaO) help to improve the devitrification resistance of glass and enhance the strength of glass; but when its content is high, the crystallization performance of glass is reduced, which is not conducive to obtaining the desired crystal phase type and grain size of microcrystalline glass. Therefore, the content of RO is 0-8%, preferably 0-5%, and more preferably 0-2%. In some embodiments, about 0%, greater than 0%, 0.01%, 0.05%, 0.1%, 0.5%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5%, 5.5%, 6%, 6.5%, 7%, 7.5%, 8% RO may be included.

_TiO2 is an optional component that helps to lower the melting temperature of glass and improve chemical stability. The present invention contains less than 5% _TiO2 , which can make the crystallization process of glass easier to control. Preferably, the content of _TiO2 is less than 3%, and more preferably less than 1%. In some embodiments, it is further preferred that _TiO2 is not contained. In some embodiments, about 0%, greater than 0%, 0.01%, 0.05%, 0.1%, 0.5%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5% _TiO2 may be contained.

In some embodiments, the ratio of the total content of ZnO, RO, _B2O3 , and _TiO2 (ZnO+RO+ _B2O3 +TiO2 ₎ to the content of _P2O5 ((ZnO+RO _{+B2O3 + TiO2} )/ _{P2O5 )} is controlled below _1.5 , which is beneficial to reducing the haze of microcrystalline glass and _{microcrystalline} glass products, improving light transmittance, and increasing the surface _stress of microcrystalline glass products. Therefore _, (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O5 is _{preferably 1.5 or} less _{, more} preferably 1.0 _{or less , more} preferably _{0.5 or} less, _{and even} more preferably _{0.2 or less} . In some embodiments, the value of (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O5 may be 0, greater than 0, 0.01, 0.05, 0.1, 0.15, 0.2, 0.25, 0.3, 0.35, 0.4, 0.45, 0.5, 0.55, 0.6, _0.65 , 0.7, 0.75, 0.8, 0.85, 0.9, 0.95, 1.0, 1.05, 1.1, 1.15, 1.2, 1.25, 1.3, 1.35, 1.4 _, 1.45, 1.5.

Ln ₂ O ₃ (Ln ₂ O ₃ is one or more of La ₂ O ₃ , Gd ₂ O ₃ , and Y ₂ O ₃ ) can reduce the difficulty of melting glass. When the content is too high, it will cause difficulty in forming crystals during glass crystallization, and the height of the drop ball test of microcrystalline glass and microcrystalline glass products will decrease. Therefore, the upper limit of the Ln ₂ O ₃ content is 5%, preferably 3%, and more preferably 1%. In some embodiments, about 0%, greater than 0%, 0.01%, 0.05%, 0.1%, 0.5%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5% of Ln ₂ O ₃ may be included.

In some embodiments, the base glass, glass-ceramics or glass-ceramics products may further contain 0-2% of a clarifier to improve the defoaming ability of the base glass, glass-ceramics or glass-ceramics products. The clarifier includes but is not limited to one or more of Sb ₂ O ₃ , SnO ₂ , SnO, F (fluorine), Cl (chlorine) and Br (bromine). Sb ₂ O ₃ and SnO ₂ are preferably used as clarifiers, and Sb ₂ O ₃ is more preferably used as clarifiers. When the above clarifiers are present alone or in combination, the upper limit of the content is preferably 1%, and the more preferably upper limit is 0.5%. In some embodiments, the amount of one or more of the above clarifying agents is about 0%, greater than 0%, 0.01%, 0.05%, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2%.

Without affecting the performance of the base glass, microcrystalline glass or microcrystalline glass products of the present invention, other components not mentioned above, such as _Yb2O3 , _Nb2O5 , _WO3 , _Bi2O3 , _Ta2O5 , _TeO2 , _GeO2 , etc., may be appropriately included. However, in order to maintain the excellent performance of the base glass, _{microcrystalline glass or microcrystalline glass products of the present invention, the individual content or total content of Yb2O3 , Nb2O5 , WO3 , Bi2O3 , Ta2O5 , TeO2 , and GeO2} is preferably less than ₅ %, more preferably less than 2%, further preferably less than 1%, and further preferably not included.

PbO and As ₂ O ₃ are toxic substances. Even a small amount of them does not meet the requirements of environmental protection. Therefore, in some embodiments of the present invention, it is preferred that PbO and As ₂ O ₃ are not included.

In some embodiments of the present invention, a colored base glass, glass-ceramic or glass-ceramic product can be prepared by including a coloring agent, and the base glass, glass-ceramic or glass-ceramic product can present different colors. Preferably, the coloring agent includes: NiO: 0-4%; and/or Ni ₂ O ₃ : 0-4%; and/or CoO: 0-2%; and/or Co ₂ O ₃ : 0-2%; and/or Fe ₂ O ₃ : 0-7%; and/or MnO ₂ : 0-4%; and/or Er ₂ O ₃ : 0-8%; and/or Nd ₂ O ₃ : 0-8%; and/or Cu ₂ O: 0-4%; and/or Pr ₂ O ₅ : 0-8%; and/or CeO ₂ : 0-4%. The weight percentage content of the coloring agent and its function are described in detail as follows:

The brown or green base glass, glass-ceramic or glass-ceramic product prepared by the present invention uses NiO, Ni ₂ O ₃ or Pr ₂ O ₅ as a colorant. NiO and Ni ₂ O ₃ are used as colorants to prepare brown or green base glass, glass-ceramic or glass-ceramic products. The two components can be used alone or in combination. Their respective contents are generally below 4%, preferably below 3%. If the content exceeds 4%, the colorant cannot be well dissolved in the base glass, glass-ceramic or glass-ceramic product. The lower limit of their respective contents is above 0.1%. If it is less than 0.1%, the base glass, glass-ceramic or glass-ceramic product will not have obvious color. In some embodiments, NiO or Ni 2 O 3 may be included in an amount of about 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%, 2.1%, 2.2%, 2.3%, 2.4%, 2.5%, 2.6%, 2.7%, 2.8%, 2.9%, 3.0%, 3.1%, 3.2%, 3.3%, 3.4%, 3.5%, 3.6%, 3.7%, 3.8%, 3.9%, 4.0%. When used in combination, the total amount of NiO and Ni ₂ O ₃ is generally less than 4%, _and the lower limit _of the total amount is above 0.1%. In some embodiments, about 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%, 2.1%, 2.2%, 2.3%, 2.4%, 2.5%, 2.6%, 2.7%, 2.8%, 2.9%, 3.0%, 3.1%, 3.2%, 3.3%, 3.4%, 3.5%, 3.6%, 3.7%, 3.8%, 3.9%, 4.0% NiO and _Ni2O3 may be _included . When _Pr2O5 is used alone as a colorant for green base glass, glass-ceramics or glass-ceramics products, the general content is below 8%, and the preferred content is _below 6%. The lower limit of the content is above 0.4%. If it is lower than 0.4%, the color of the base glass, glass-ceramics or glass-ceramics products will not be obvious. In some embodiments, about 0.4%, 0.6%, 0.8%, 1.0%, 1.2%, 1.4%, 1.6%, 1.8%, 2.0%, 2.2%, 2.4%, 2.6%, 2.8%, 3.0%, 3.2%, 3.4%, 3.6%, 3.8%, 4.0%, 4.2%, 4.4%, 4.6%, 4.8%, 5.0%, 5.2%, 5.4%, 5.6%, 5.8%, 6.0%, 6.2%, 6.4%, 6.6%, 6.8%, 7.0%, 7.2%, 7.4%, 7.6%, 7.8%, 8.0 _{% Pr2O5} can be included.

The blue base glass, microcrystalline glass or _{microcrystalline} glass products prepared by the present invention use CoO or _Co2O3 as a colorant. The two colorant components can be used alone or in combination. Their respective contents are generally below 2%, preferably below 1.8%. If the content exceeds 2%, the colorant cannot be well dissolved in the base glass, microcrystalline glass or microcrystalline glass products. The lower limit of their respective contents is above 0.05%. If it is lower than 0.05%, the color of the base glass, microcrystalline glass or microcrystalline glass products is not obvious. In some embodiments, about 0.05%, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0% of CoO or Co ₂ O ₃ may be included. When used in combination, the total amount of CoO and Co ₂ O ₃ does not exceed 2%, and the lower limit of the total amount is above 0.05%. In some embodiments, about 0.05%, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0% _CoO and _Co2O3 may be included.

The yellow base glass, glass-ceramics or glass-ceramics products prepared by the present invention use _Cu2O or _CeO2 as a colorant. The two colorant components are used alone or in combination, and their respective content lower limits are above 0.5%. If they are lower than 0.5%, the color of the base glass, glass-ceramics or glass-ceramics products is not obvious. _Cu2O is used alone at a content of less than 4%, preferably less than 3%. If the content exceeds 4%, the base glass is likely to crystallize. In some embodiments, about 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%, 2.1%, 2.2%, 2.3%, 2.4%, 2.5%, 2.6%, 2.7%, 2.8%, 2.9%, 3.0%, 3.1%, 3.2%, 3.3%, 3.4%, 3.5%, 3.6%, 3.7%, 3.8%, 3.9%, 4.0% Cu ₂ O may be included. The CeO ₂ content alone is generally 4% or less, preferably 3% or less. If the content exceeds 4%, the base glass, microcrystalline glass or microcrystalline glass products will have poor gloss. In some embodiments, CeO 2 may be included in an amount of about 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%, 2.1%, 2.2%, 2.3%, 2.4%, 2.5%, 2.6%, 2.7%, 2.8%, 2.9%, 3.0%, 3.1%, 3.2%, 3.3%, 3.4%, 3.5%, 3.6%, 3.7%, 3.8%, 3.9%, _4.0 %. If two coloring agents are mixed, the total amount is generally less than 4%, and the lower limit of the total amount is more than 0.5%. In some embodiments, about 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%, 2.1%, 2.2%, 2.3%, 2.4%, 2.5%, 2.6%, 2.7%, 2.8%, 2.9%, 3.0%, 3.1%, 3.2%, 3.3%, 3.4%, 3.5%, 3.6%, 3.7%, 3.8%, 3.9%, 4.0% _CeO2 and _Cu2O may be included.

The black or smoke gray base glass, microcrystalline glass or microcrystalline glass products prepared by the present invention use _Fe2O3 alone as a colorant; or use a colorant that is _a mixture of _Fe2O3 and CoO _; or use a _colorant that is a mixture of _Fe2O3 and _{Co2O3 ;} or use a colorant that is a mixture of _Fe2O3 , _CoO and NiO; or use a colorant that is a mixture of _Fe2O3 , _Co2O3 and NiO. The colorant used to prepare the black and _smoke gray base glass, _{microcrystalline} glass or microcrystalline glass products mainly uses _Fe2O3 . ₃ coloring, the content is 7% or less, preferably 5% or less, and the lower limit of the content is above 0.2%. In some embodiments, it can include about 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%, 2.1%, 2.2%, 2.3%, 2.4%, 2.5%, 2.6%, 2.7%, 2.8%, 2.9%, 3.0%, 3.1%, 3.2%, 3.3%, 3.4%, 3.5%, 3.6%, 3.7%, 3.8%, 3.9%, 4.0%, 4.5%, 5.0%, 5.5%, 6.0%, 6.5%, _7.0 % _Fe2O3 . CoO and Co ₂ O ₃ absorb visible light and can deepen the coloring of base glass, glass-ceramics or glass-ceramics products. Generally, when mixed with Fe ₂ O ₃ , their respective contents are less than 0.6%, and the lower limit is above 0.2%. In some embodiments, about 0.2%, 0.3%, 0.4%, 0.5%, 0.6% of CoO and/or Co ₂ O ₃ may be included. NiO absorbs visible light and can deepen the coloring of base glass, glass-ceramics or glass-ceramics products. Generally, when mixed, its content is less than 1%, and the lower limit of the total amount is above 0.2%. In some embodiments, about 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0% of NiO may be included.

The purple base glass, glass-ceramics or glass-ceramics products prepared by the present invention use _MnO2 as a colorant, and the content is generally below 4%, preferably below 3%, and the lower limit of the content is above 0.1%. If it is lower than 0.1%, the color of the base glass, glass-ceramics or glass-ceramics products is not obvious. In some embodiments, about 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%, 2.1%, 2.2%, 2.3%, 2.4%, 2.5%, 2.6%, 2.7%, 2.8%, 2.9%, 3.0%, 3.1%, 3.2%, 3.3%, 3.4%, 3.5%, 3.6%, 3.7%, 3.8%, 3.9%, 4.0% _MnO2 may be included.

The pink base glass, glass-ceramic or glass-ceramic product prepared by the present invention uses Er ₂ O ₃ as a coloring agent, and the content of Er 2 O 3 is generally below 8%, preferably below 6%. Since the rare earth element Er ₂ O ₃ has a low coloring efficiency, when the content exceeds 8%, the color of the base glass, glass-ceramic or glass-ceramic product cannot be further deepened, but the cost is increased. The lower limit of the content is above 0.4%. If it is lower than 0.4%, the color of the base glass, glass-ceramic or glass-ceramic product is not obvious. In some embodiments, Er2O3 may be included in an amount of about 0.4%, 0.6%, 0.8%, 1.0%, 1.2%, 1.4%, 1.6%, 1.8%, 2.0%, 2.2%, 2.4%, 2.6%, 2.8%, 3.0%, 3.2%, 3.4%, 3.6%, 3.8%, 4.0%, 4.2%, 4.4%, 4.6%, 4.8%, 5.0%, 5.2%, 5.4%, 5.6%, 5.8%, 6.0%, 6.2%, 6.4%, 6.6%, 6.8%, 7.0%, 7.2%, 7.4%, 7.6%, _7.8 %, _8.0 %.

The purple-red base glass, glass-ceramic or glass-ceramic product prepared by the present invention uses Nd ₂ O ₃ as a coloring agent, and the content of Nd 2 O 3 is generally below 8%, preferably below 6%. Since the rare earth element Nd ₂ O ₃ has low coloring efficiency, the use of a content exceeding 8% cannot further deepen the color of the base glass, glass-ceramic or glass-ceramic product, but increases the cost. The lower limit of the content is above 0.4%. If it is lower than 0.4%, the color of the base glass, glass-ceramic or glass-ceramic product is not obvious. In some embodiments, about 0.4%, 0.6%, 0.8%, 1.0%, 1.2%, 1.4%, 1.6%, 1.8%, 2.0%, 2.2%, 2.4%, 2.6%, 2.8%, 3.0%, 3.2%, 3.4%, 3.6%, 3.8%, 4.0%, 4.2%, 4.4%, 4.6%, 4.8%, 5.0%, 5.2%, 5.4%, 5.6%, 5.8%, 6.0%, 6.2%, 6.4%, 6.6%, 6.8%, 7.0%, 7.2%, 7.4%, 7.6%, 7.8%, 8.0% _{Nd2O3 may} be included.

The red matrix glass, _{microcrystalline} glass or microcrystalline glass products prepared by the present invention use a mixed coloring agent of _Er2O3 , _Nd2O3 and _{MnO2 .} The Er ions in the glass have absorption at 400-500nm, the Mn ions mainly have absorption at 500nm, and the Nd ions mainly have strong absorption at 580nm. The mixture of the three substances can prepare red matrix glass, microcrystalline glass or microcrystalline glass products. Since _Er2O3 and _Nd2O3 are rare _natural colors and have relatively weak coloring ability, the usage amount of _Er2O3 is within 6%, the usage amount _{of Nd2O3} is within 4%, _{and MnO2} has strong _coloring and the usage amount is within the range of 2%. The lower limit of the total amount of the mixed coloring agent used is above 0.9%.

The "does not contain" and "0%" recorded in this article mean that the compound, molecule or element is not intentionally added as a raw material to the base glass, microcrystalline glass or microcrystalline glass product of the present invention; however, as the raw materials and/or equipment for producing base glass, microcrystalline glass or microcrystalline glass products, there may be certain impurities or components that are not intentionally added, which may be contained in a small amount or trace amount in the final base glass, microcrystalline glass or microcrystalline glass product, and this situation is also within the scope of protection of the patent of the present invention.

In some embodiments of the present invention, the crystal phase in the glass-ceramics and glass-ceramics products includes a nepheline crystal phase, which provides high strength for the glass-ceramics and glass-ceramics products of the present invention, and the drop ball test height and four-point bending strength of the glass-ceramics and glass-ceramics products become larger. In some embodiments, the glass-ceramics or glass-ceramics products include a lithium nepheline crystal phase, in some embodiments, the glass-ceramics or glass-ceramics products include a sodium nepheline crystal phase, and in some embodiments, the glass-ceramics or glass-ceramics products include both lithium nepheline and sodium nepheline crystal phases. The glass-ceramics of the present invention have excellent chemical strengthening properties, and can also be processed into glass-ceramics products through a chemical strengthening process to obtain excellent mechanical strength. Through reasonable component design, the glass-ceramics and glass-ceramics products of the present invention can obtain appropriate grain size, so that the glass-ceramics and glass-ceramics products of the present invention have high strength. The glass-ceramics and glass-ceramics products of the present invention have an appropriate content of crystalline phase, so that the glass-ceramics and glass-ceramics products of the present invention have excellent mechanical properties.

The grain size and crystalline phase type of the glass-ceramic or glass-ceramic product of the present invention will affect the haze and light transmittance of the glass-ceramic or glass-ceramic product. In some embodiments, the haze of a glass-ceramic product or glass-ceramic with a thickness of less than 1 mm is less than 0.15%, preferably less than 0.12%, and more preferably less than 0.10%. In some embodiments, the grain size of the glass-ceramic product or glass-ceramic is less than 80 nm, preferably less than 60 nm, and more preferably less than 50 nm.

In some embodiments, the crystalline content and refractive index of the glass-ceramic or glass-ceramic product of the present invention affect the |B| value of the glass-ceramic or glass-ceramic product. When the glass-ceramic or glass-ceramic product is observed in the visible light range, it appears bluish or yellowish, affecting the optical properties of the product, and is indicated by the |B| value in LAB (chromaticity value of material color). The glass-ceramic or glass-ceramic product of the present invention exhibits a low |B| value in the visible light range. In some embodiments, the average optical |B| value of a glass-ceramic product or glass-ceramic with a thickness of less than 1 mm at 400 to 800 nm is less than 1.5, preferably less than 1.0, and more preferably less than 0.8.

In some embodiments, the glass-ceramics or glass-ceramics products of the present invention exhibit high transparency in the visible light range (i.e., the glass-ceramics or glass-ceramics products are transparent). The glass-ceramics or glass-ceramics products exhibit high transmittance in the visible light range. In some preferred embodiments, the light transmittance of the glass-ceramics products or glass-ceramics with a thickness of less than 1 mm at 550 nm is preferably 88% or more, more preferably 89% or more, and further preferably 90% or more.

In some embodiments, antimicrobial components can be added to the base glass, glass-ceramic, or glass-ceramic products. The glass-ceramic or glass-ceramic products described herein can be used in applications such as kitchen or catering countertops, where exposure to harmful bacteria is likely. The antimicrobial components contained in the base glass, glass-ceramic, or glass-ceramic products include but are not limited to Ag, AgO, Cu, CuO, Cu ₂ O, etc. In some embodiments, the content of the above antimicrobial components alone or in combination is less than 2%, preferably less than 1%.

The base glass, glass-ceramics and glass-ceramics products of the present invention can be produced and manufactured by the following method:

To form the matrix glass: the raw materials are mixed evenly according to the proportion of the components, the uniform mixture is placed in a platinum or quartz crucible, and melted in an electric furnace or a gas furnace at a temperature range of 1250 to 1650°C for 5 to 24 hours, depending on the melting difficulty of the glass components. After stirring to make it uniform, it is cooled to an appropriate temperature and cast into a mold, and then slowly cooled.

The base glass of the present invention can be formed by well-known methods.

The base glass of the present invention is crystallized through a crystallization process after forming or forming processing, and crystals are uniformly precipitated inside the glass. The crystallization process can be carried out through one stage or two stages, and it is preferred to carry out the crystallization process in two stages. The nucleation process is carried out at a first temperature, and then the crystal growth process is carried out at a second temperature higher than the nucleation process temperature. The crystallization process carried out at the first temperature is called the first crystallization process, and the crystallization process carried out at the second temperature is called the second crystallization process.

In order to obtain the desired physical properties of glass-ceramics, the preferred crystallization process is:

The above-mentioned crystallization treatment is carried out in one stage, and the nucleation process and the crystal growth process can be carried out continuously. That is, the temperature is raised to a specified crystallization treatment temperature, and after reaching the crystallization treatment temperature, the temperature is maintained for a certain time, and then the temperature is lowered. The crystallization treatment temperature is preferably 580-750°C, and in order to precipitate the desired crystal phase, it is more preferably 600-700°C. The holding time at the crystallization treatment temperature is preferably 0-8 hours, and more preferably 1-6 hours.

When the crystallization treatment is performed in two stages, the first temperature is preferably 500 to 620° C., and the second temperature is preferably 620 to 750° C. The holding time at the first temperature is preferably 0 to 24 hours, more preferably 2 to 15 hours. The holding time at the second temperature is preferably 0 to 10 hours, more preferably 0.5 to 6 hours.

The above holding time of 0 hours means that the temperature starts to drop or rise again within less than 1 minute after reaching the temperature.

In some embodiments, the base glass or glass-ceramics described herein may be formed into a shaped body by various processes, including but not limited to sheets, and the processes include but are not limited to slit drawing, float process, roll pressing, and other processes known in the art for forming sheets. Alternatively, the base glass or glass-ceramics may be formed by float process or roll pressing. The shaped body of the present invention also includes lenses, prisms, etc.

The base glass or microcrystalline glass of the present invention can be processed by grinding or polishing to produce a glass molded body or microcrystalline glass molded body in the form of a sheet, but the method of producing a glass molded body or microcrystalline glass molded body is not limited to these methods.

The base glass or microcrystalline glass of the present invention can be prepared into glass molded bodies or microcrystalline glass molded bodies of various shapes by a hot bending process or a pressing process at a certain temperature, but is not limited to these methods.

In some embodiments, a glass forming body or a glass-ceramic forming body can be manufactured by a hot bending process. The hot bending process is a process in which 2D or 2.5D glass or glass-ceramic is placed in a mold and a process including preheating, pressurizing, molding, and cooling under pressure is performed in a hot bending machine to obtain a glass forming body or glass-ceramic forming body with a 3D curved surface.

In some embodiments, the glass-ceramic body has a 2.5D or 3D configuration, i.e., the glass-ceramic body has a non-planar configuration. As used herein, "non-planar configuration" means that in a 2.5D or 3D shape, at least a portion of the glass-ceramic body extends outward or along an angle with a plane defined by the original, layout configuration of the 2D base glass. A 2.5D or 3D glass-ceramic body formed from a base glass may have one or more protrusions or curved portions.

In some embodiments, the method for manufacturing a glass-ceramic molded body is a hot bending process method in combination with the characteristics of the growth and transformation of the crystal phase in the glass-ceramic. Specifically, the method includes pre-crystallization and hot working forming. The pre-crystallization described in the present invention is to form a pre-crystallized glass through a controlled crystallization process of the matrix glass, and the crystallinity of the pre-crystallized glass does not reach the crystallinity required by the performance index of the target glass-ceramic molded body. The pre-crystallized glass is then formed into a glass-ceramic molded body through a hot working forming process.

In some embodiments, a method for manufacturing a glass-ceramic formed body comprises the following steps:

1) subjecting the base glass to a crystallization heat treatment process, including heating, heat preservation nucleation, heating, heat preservation crystallization, and cooling to room temperature to form pre-crystallized glass;

2) The pre-crystallized glass is subjected to heat processing to obtain a glass-ceramic formed body.

The crystallization heat treatment process described in the present invention includes nucleating the base glass at a certain temperature _Th and time _th , and then crystallizing at a certain temperature _Tc and time _tc . The crystallinity of the obtained pre-crystallized glass does not reach the crystallinity required by the performance indicators of the target microcrystalline glass forming body. Using the XRD test data, the total content of the main crystalline phase in the crystallinity of the pre-crystallized glass is calculated to be I _c1 through the Rietveld full spectrum fitting precision method. The pre-crystallization of the present invention is a complete process from a process point of view, including a nucleation process step, a crystallization process of one, two or three or more stages, etc. It is a complete process from heating, heat preservation, heating again, heat preservation..., and then cooling down to room temperature in steps. Different from the primary crystallization, secondary crystallization, etc. mentioned in some documents or patents, the present invention is actually only the first crystallization, the second crystallization, etc. in a complete crystallization process, which are continuous and there is no process of cooling to room temperature and then heating up again for crystallization.

The heat forming process mentioned in the present invention refers to the heat forming process of the pre-crystallized glass under certain temperature, time, pressure and other conditions. The heat forming process includes more than one heat forming process, and the heat forming process includes but is not limited to press forming, bending forming or drawing forming of the pre-crystallized glass under certain temperature, time, pressure and other conditions. In the heat forming process, sometimes a complex shaped body cannot be completed by one heat forming process, and may need to be heat formed twice or more.

In some embodiments, the method for manufacturing a glass-ceramic formed body is a hot bending process method. Specifically, in some embodiments, the method for manufacturing a glass-ceramic formed body comprises the following steps:

1) Heating and preheating: Place the base glass or pre-crystallized glass or microcrystalline glass in the mold, and the mold passes through each heating station in the hot bending machine in turn, and stays at each station for a certain period of time to keep warm. The temperature in the preheating zone is 400-800°C, the pressure is 0.01-0.05MPa, and the time is 40-200s. In some implementations, for a hot bending machine with 5 preheating stations, the initial temperature is generally set at around 500°C, and the subsequent stations gradually increase the temperature. The temperature gradient between the two adjacent stations gradually decreases from low temperature to high temperature, and the temperature difference between the last preheating station and the first pressing station is within 20°C.

2) Pressurized molding: After preheating, the mold is transferred to the molding station. The hot bending machine applies a certain pressure to the mold. The pressure range is 0.1-0.8Mpa. The pressure is determined according to factors such as glass thickness and curvature. The molding station temperature range is 650-850℃, and the molding time range is 40-200s.

3) Pressure-maintaining cooling: The mold is transferred to the cooling station for cooling step by step. The cooling temperature range is controlled at 750-500℃, the pressure is 0.01-0.05Mpa, and the time is 40-200s.

In addition to controlling the appearance quality of ordinary high-aluminum glass, the hot-bending process of forming glass-ceramic bodies also requires controlling the impact of crystal growth during the hot-bending process on the performance of the glass-ceramic. For example, 3D curved glass-ceramic used for display devices or electronic equipment casings requires close attention to light transmittance, haze, |B| value and uniformity after hot bending.

The amount of crystal phase change before and after hot bending determines the size uniformity, mass production feasibility and cost control of the microcrystalline glass formed body. The base glass and microcrystalline glass of the present invention have excellent thermal processing performance. After hot bending, the change in crystal phase content is less than 20%, preferably less than 15%, and further preferably less than 10%, which can ensure the uniformity of the haze and |B| value of the microcrystalline glass formed body obtained after hot bending.

The substrate glass, glass-ceramic and glass-ceramic products described in the present invention can have any reasonable and useful thickness.

In addition to improving the mechanical properties by precipitating crystals, the microcrystalline glass of the present invention can also obtain better mechanical properties by forming a compressive stress layer, thereby manufacturing microcrystalline glass products.

In some embodiments, the base glass or glass-ceramics can be processed into sheets and/or shaped (such as punching, hot bending, etc.), polished and/or polished after shaping, and then chemically strengthened through a chemical strengthening process to form a glass-ceramics product. In some embodiments, the glass-ceramics formed body can be chemically strengthened through a chemical strengthening process to form a glass-ceramics product.

The chemical strengthening described in the present invention is the ion exchange method. During the ion exchange process, smaller metal ions in the matrix glass or glass-ceramic or glass-ceramic body are replaced or "exchanged" by larger metal ions of the same valence state near the matrix glass or glass-ceramic or glass-ceramic body. The replacement of smaller ions with larger ions creates compressive stress on the surface of the matrix glass or glass-ceramic or glass-ceramic body and tensile stress inside.

In some embodiments, the metal ions are monovalent alkali metal ions (e.g., Na ⁺ , K ⁺ , Rb ⁺ , Cs ⁺ , etc.), and the ion exchange is performed by immersing the matrix glass or glass-ceramic or glass-ceramic body in a salt bath containing at least one molten salt of larger metal ions, and the larger metal ions are used to replace smaller metal ions in the matrix glass or glass-ceramic or glass-ceramic body. Alternatively, other monovalent metal ions such as Ag ⁺ , Tl ⁺ , Cu ⁺ , etc. can also be used to exchange monovalent ions. One or more ion exchange processes used to chemically strengthen the base glass or glass-ceramic or glass-ceramic formed body may include, but are not limited to, immersing it in a single salt bath, or immersing it in multiple salt baths of the same or different compositions with washing and/or annealing steps between immersions.

In some embodiments, the matrix glass or glass-ceramic or glass-ceramic body can be ion exchanged by immersing in a salt bath of molten Na salt (such as NaNO ₃ ) at a temperature of about 350-470° C. for about 1-36 hours, preferably at a temperature range of 380-460° C., and preferably for a time range of 2-10 hours. In this embodiment, Na ions replace part of the Li ions in the matrix glass or glass-ceramic or glass-ceramic body, thereby forming a surface compression layer and exhibiting high mechanical properties. In some embodiments, the matrix glass or glass-ceramic or glass-ceramic body can be ion-exchanged by immersing it in a salt bath of molten K salt (such as KNO ₃ ) at a temperature of about 360-450° C. for 1-36 hours, preferably for a time range of 1-10 hours. In some embodiments, the matrix glass or glass-ceramic or glass-ceramic body can be ion-exchanged by immersing it in a mixed salt bath of molten K salt and Na salt at a temperature of about 360-450° C. for 1-36 hours, preferably for a time range of 2-24 hours.

The various performance indicators of the glass-ceramics or glass-ceramics products of the present invention are tested by the following methods:

[Fog]

The Konica Minolta CM-3600A spectrophotometer was used to prepare samples with a diameter of less than 1 mm and tested according to the GB2410-80 standard.

[Grain size]

Using a SEM scanning electron microscope for measurement, the microcrystalline glass is surface treated in HF acid, and then the surface of the microcrystalline glass is gold-sprayed. The surface is scanned under a SEM scanning electron microscope to determine the size of its grains.

[Light transmittance]

The light transmittance described in this article is external transmittance, sometimes referred to as transmittance.

The samples were processed to a thickness of less than 1 mm and parallel polished on opposite surfaces. The light transmittance at 550 nm was measured using a Konica Minolta CM-3600A spectrophotometer.

[Surface stress] and [ion exchange layer depth]

The surface stress was measured using a glass surface stress meter SLP-2000.

The depth of the ion exchange layer was measured using a glass surface stress meter SLP-2000.

The measurement conditions were that the sample's refractive index was 1.56 and the optical elastic constant was 24.5 [(nm/cm )/Mpa].

[Drop ball test height]

Place a glass-ceramic product sample with a length and width of 150mm×73mm and a thickness of less than 1mm on a glass support fixture, and drop a 132g steel ball from a specified height. The maximum drop ball test height is the impact that the sample can withstand without breaking. Specifically, the test starts at a drop ball test height of 400mm. Without breaking, the height is changed in sequence through 400mm, 500mm, 600mm, 700mm and above, with an interval of 100mm each time. For the embodiment with a "drop ball test height", the glass-ceramic product is the test object. The test data recorded as 1600mm in the embodiment indicates that the sample withstood an impact of 1500mm without breaking, and broke when it was raised to 1600mm for the test, so the drop ball test height is 1600mm. In the present invention, the drop ball test height is sometimes referred to as the drop ball height.

[Body drop height]

Place a glass-ceramic sample with a length and width of 150mm×73mm and a thickness of less than 1mm on a glass holder, and drop a 32g steel ball from a specified height. The maximum drop ball test height that the sample can withstand without breaking is the main body drop ball height. Specifically, the test starts at a drop ball test height of 400mm, and changes the height in sequence through 400mm, 500mm, 600mm, 700mm and above without breaking, with an interval of 100mm each time. For the embodiment with a "main body drop ball height", the glass-ceramic is used as the test object, which is the drop ball test height of the glass-ceramic. The test data recorded as 1300mm in the embodiment indicates that the sample withstood an impact of 1200mm without breaking, but broke when the test height was raised to 1300mm, so the main body drop height is 1300mm.

[Four-point bending strength]

The microcomputer-controlled electronic universal testing machine CMT6502 is used, and the sample specification is less than 1mm thick, and the test is carried out according to ASTM C158-2002. In the present invention, the four-point bending strength is sometimes referred to as the bending strength.

[Vickers hardness]

The value expressed as the load when a diamond square cone indenter with a relative surface angle of 136° is pressed into the test surface into a pyramid-shaped depression divided by the surface area ( ^mm2 ) calculated from the length of the depression. The test load is 200g and the holding time is 20 seconds. In the present invention, Vickers hardness is sometimes referred to as hardness.

[|B|value]

Use Konica Minolta CM-700d to test the B value. The sample specification is less than 1mm thick. Use the matching calibration long and short tubes to perform instrument zero calibration and white plate calibration respectively. After calibration, use the long tube to perform air test to determine the stability and calibration reliability of the instrument (B≤0.05). After the instrument is calibrated, place the product on the zero long tube for testing.

The |B| value is the absolute value of B.

The glass-ceramic product of the present invention has the following properties:

1) In some embodiments, the four-point bending strength of a glass-ceramic product with a thickness of less than 1 mm is 700 MPa or more, preferably 750 MPa or more, and more preferably 800 MPa or more. The thickness is preferably 0.2-1 mm, more preferably 0.3-0.9 mm, further preferably 0.5-0.8 mm, and further preferably 0.55 mm, 0.6 mm, 0.68 mm, 0.7 mm, or 0.75 mm.

2) In some embodiments, the depth of the ion exchange layer of the microcrystalline glass product is greater than 50 μm, preferably greater than 60 μm, more preferably greater than 80 μm, and further preferably greater than 100 μm.

3) In some embodiments, the drop ball test height of a glass-ceramic product with a thickness of less than 1 mm is 1100 mm or more, preferably 1300 mm or more, and more preferably 1500 mm or more. The thickness is preferably 0.2-1 mm, more preferably 0.3-0.9 mm, further preferably 0.5-0.8 mm, and further preferably 0.55 mm, 0.6 mm, 0.68 mm, 0.7 mm, or 0.75 mm.

4) In some embodiments, the Vickers hardness (H _v ) of the microcrystalline glass product is 750 kgf/mm ² or more, preferably 780 kgf/mm ² or more, more preferably 800 kgf/mm ² or more, and further preferably 810 kgf/mm ² or more.

5) In some embodiments, the grain size of the microcrystalline glass product is less than 80nm, preferably less than 60nm, more preferably less than 50nm, and further preferably less than 40nm.

6) In some embodiments, the surface stress of the microcrystalline glass product is greater than 150 MPa, preferably greater than 170 MPa, and more preferably greater than 190 MPa.

7) In some embodiments, the haze of a glass-ceramic product with a thickness of less than 1 mm is less than 0.15%, preferably less than 0.12%, and more preferably less than 0.10%. The thickness is preferably 0.2-1 mm, more preferably 0.3-0.9 mm, further preferably 0.5-0.8 mm, and further preferably 0.55 mm, 0.6 mm, 0.68 mm, 0.7 mm, or 0.75 mm.

8) In some embodiments, the light transmittance of the microcrystalline glass product with a thickness of less than 1 mm at a wavelength of 550 nm is 88% or more, preferably 89% or more, more preferably 90% or more, and further preferably 91% or more. The thickness is preferably 0.2-1 mm, more preferably 0.3-0.9 mm, further preferably 0.5-0.8 mm, and further preferably 0.55 mm, 0.6 mm, 0.68 mm, 0.7 mm, or 0.75 mm.

9) In some embodiments, for a glass-ceramic product having a thickness of less than 1 mm, the average optical |B| value at 400-800 nm is less than 1.5, preferably less than 1.0, and more preferably less than 0.8. The thickness is preferably 0.2-1 mm, more preferably 0.3-0.9 mm, further preferably 0.5-0.8 mm, and further preferably 0.55 mm, 0.6 mm, 0.68 mm, 0.7 mm, or 0.75 mm.

The microcrystalline glass of the present invention has the following properties:

1) In some embodiments, the grain size of the microcrystalline glass is less than 80 nm, preferably less than 60 nm, more preferably less than 50 nm, and further preferably less than 40 nm.

2) In some embodiments, the haze of glass-ceramics with a thickness of 1 mm or less is 0.15% or less, preferably 0.12% or less, and more preferably 0.10% or less. The thickness is preferably 0.2-1 mm, more preferably 0.3-0.9 mm, further preferably 0.5-0.8 mm, and further preferably 0.55 mm, 0.6 mm, 0.68 mm, 0.7 mm, or 0.75 mm.

3) In some embodiments, the light transmittance of the microcrystalline glass with a thickness of less than 1 mm at a wavelength of 550 nm is 88% or more, preferably 89% or more, more preferably 90% or more, and further preferably 91% or more. The thickness is preferably 0.2-1 mm, more preferably 0.3-0.9 mm, further preferably 0.5-0.8 mm, and further preferably 0.55 mm, 0.6 mm, 0.68 mm, 0.7 mm, or 0.75 mm.

4) In some embodiments, the ball drop height of the microcrystalline glass with a thickness of less than 1 mm is 1000 mm or more, preferably 1200 mm or more, and more preferably 1400 mm or more. The thickness is preferably 0.2-1 mm, more preferably 0.3-0.9 mm, further preferably 0.5-0.8 mm, and further preferably 0.55 mm, 0.6 mm, 0.68 mm, 0.7 mm, or 0.75 mm.

5) In some embodiments, for glass-ceramics with a thickness of less than 1 mm, the average optical |B| value at 400-800 nm is less than 1.5, preferably less than 1.0, and more preferably less than 0.8. The thickness is preferably 0.2-1 mm, more preferably 0.3-0.9 mm, further preferably 0.5-0.8 mm, and further preferably 0.55 mm, 0.6 mm, 0.68 mm, 0.7 mm, or 0.75 mm.

6) In some embodiments, the Vickers hardness (H _v ) of the glass-ceramics is greater than 650 kgf/mm ² , preferably greater than 680 kgf/mm ² , and more preferably greater than 700 kgf/mm ² .

The glass-ceramics, glass-ceramics products, base glass, glass forming bodies, and glass-ceramics forming bodies of the present invention can be widely made into glass cover plates or glass components due to the above-mentioned excellent properties; at the same time, the glass-ceramics, glass-ceramics products, base glass, glass forming bodies, and glass-ceramics forming bodies of the present invention can be applied to electronic devices or display devices, such as mobile phones, watches, computers, touch display screens, etc., for The manufacture of protective glass for mobile phones, smart phones, tablet computers, laptops, PDAs, televisions, personal computers, MTA machines or industrial displays; or for the manufacture of touch screens, protective windows, car windows, train windows, aircraft machinery windows, touch screen protective glass; or for the manufacture of hard disk substrates or solar battery substrates; or for the manufacture of white goods, such as refrigerator parts or kitchenware.

Embodiment

In order to further clearly explain and illustrate the technical solution of the present invention, the following non-limiting examples are provided. The present invention has been tried to ensure the accuracy of the numerical values, but some errors and deviations must be taken into account. The composition of the microcrystalline glass or microcrystalline glass products is given in weight % based on the oxides and has been standardized to 100%.

＜Glass-ceramic Example＞

This embodiment adopts the above-mentioned method for manufacturing microcrystalline glass to obtain microcrystalline glass having the composition shown in Tables 1 to 3. In addition, the characteristics of each microcrystalline glass are measured by the test method described in the present invention, and the measurement results are shown in Tables 1 to 3. In the following embodiments, the thickness of the test sample used for the body drop ball height, haze, light transmittance, |B| value, etc. is 0.7 mm.

Table 1. Example (wt%) 1# 2# 3# 4# 5# 6# 7# 8# SiO ₂ 48.3 49.4 42.5 47.8 52.9 45 41.1 43.3 Al ₂ O ₃ 22.5 24.6 34.3 23.2 25.3 35.2 20.5 21.8 _Li2O 5.2 3.7 6.5 13.4 4.5 2.5 12.4 10.3 _Na2O 11.3 12.4 5.6 4.3 6.6 7.2 15.1 13.7 _K2O 0.5 1.3 0.2 1.1 0.6 2.5 3.4 1.8 _{P2O5 ​} 6.2 5.4 8.5 2.8 1.5 4.3 3.8 5.2 ZrO ₂ 2.7 1.5 0.4 4.3 5.2 2.4 1.5 1.7 ZnO 2 0 0 0 0 0 0 0 _{B2O3 ​} 0 0 1.5 0 2 0 0.5 0 MgO 0 1 0 0 0 0.5 0 0 CaO 0 0 0 0.5 0 0 0 0 SrO 0 0 0 0 0 0 0 0 BaO 0 0 0 0 0 0 1.2 0.8 _TiO2 1 0.5 0 2 0 0 0 0 La ₂ O ₃ 0 0 0 0 0 0 0 1 _{Y2O3 ​} 0 0 0 0 1 0 0 0 _{Gd2O3 ​} 0 0 0 0 0 0 0 0 _{Sb2O3 ​} 0.3 0.2 0.5 0.6 0.4 0.3 0.5 0.4 _SnO2 0 0 0 0 0 0.1 0 0 SnO 0 0 0 0 0 0 0 0 _CeO2 0 0 0 0 0 0 0 0 Total 100 100 100 100 100 100 100 100 P ₂ O ₅ +ZrO ₂ 8.9 6.9 8.9 7.1 6.7 6.7 5.3 6.9 (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ 5.452 6.852 4.694 9.821 21.27 9.86 9.368 6.827 SiO ₂ /Al ₂ O ₃ 2.147 2.008 1.239 2.06 2.091 1.278 2.005 1.986 SiO ₂ / (Na ₂ O + B ₂ O ₃ ) 4.274 3.984 5.986 11.12 6.151 6.25 2.635 3.161 ( _Na2O + _Li2O )/ _SiO2 0.342 0.326 0.285 0.37 0.21 0.216 0.669 0.554 (ZrO ₂ +ZnO)/Na ₂ O 0.416 0.121 0.071 1 0.788 0.333 0.099 0.124 (P ₂ O ₅ +Na ₂ O)/Li ₂ O 3.365 4.811 2.169 0.53 1.8 4.6 1.524 1.835 (ZnO+RO+B ₂ O ₃ +TiO ₂ )/ P ₂ O ₅ 0.484 0.278 0.176 0.893 1.333 0.116 0.447 0.154 K ₂ O/ZrO ₂ 0.185 0.867 0.5 0.256 0.115 1.042 2.267 1.059 Crystalline Phase Lithium nepheline, sodium nepheline Sodium nepheline Lithium nepheline, sodium nepheline Lithium Nephrite Lithium nepheline, sodium nepheline Lithium nepheline, sodium nepheline Lithium nepheline, sodium nepheline Lithium nepheline, sodium nepheline Grain size (nm) 35 28 30 35 40 32 50 30 Fog (%) 0.10 0.10 0.08 0.13 0.14 0.09 0.12 0.08 Light transmittance at 550nm wavelength (%) 90.8 91.2 91.5 91.3 90.3 91.5 91.0 91.6 |B| value 1.0 1.1 0.9 0.9 0.7 1.2 0.7 0.6 H _v (kgf/mm ² ) 683 692 688 690 678 692 694 695 Body drop ball height (mm) 1400 1400 1300 1200 1200 1400 1400 1400

Table 2. Example (wt%) 9# 10# 11# 12# 13# 14# 15# 16# SiO ₂ 43.5 44.4 55 43.5 48 47.5 46.2 47.3 Al ₂ O ₃ 23.2 24.3 23.5 32.4 30 26.6 27.8 29.4 _Li2O 8.6 11.2 5.8 6.6 6.2 7.5 7.2 7 _Na2O 8.4 8.1 7.3 7.8 9 8.5 8.8 7.9 _K2O 4.3 2.2 0.8 1.6 1.4 2 2.3 1.7 _{P2O5 ​} 7.4 4 4.6 3.5 2.7 5.1 5.7 4.2 ZrO ₂ 0.8 1.1 1.9 3.3 2.5 2.3 1.6 1.8 ZnO 0 0 0.5 1 0 0 0 0.2 _{B2O3 ​} 3 0 0 0 0 0 0 0 MgO 0 0 0 0 0 0 0 0 CaO 0 0 0 0 0 0 0 0 SrO 0 0 0 0 0 0 0 0 BaO 0 1 0 0 0 0 0 0 _TiO2 0 3 0 0 0 0 0 0 La ₂ O ₃ 0 0 0 0 0 0 0 0 _{Y2O3 ​} 0.5 0 0 0 0 0 0 0 _{Gd2O3 ​} 0 0.5 0 0 0 0 0 0 _{Sb2O3 ​} 0.3 0.2 0.1 0 0.2 0.5 0.4 0.5 _SnO2 0 0 0.5 0.3 0 0 0 0 SnO 0 0 0 0 0 0 0 0 _CeO2 0 0 0 0 0 0 0 0 Total 100 100 100 100 100 100 100 100 P ₂ O ₅ +ZrO ₂ 8.2 5.1 6.5 6.8 5.2 7.4 7.3 6 (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ 4.27 8.1 6.696 11.49 14.44 6.882 6.421 8.881 SiO ₂ /Al ₂ O ₃ 1.875 1.827 2.34 1.343 1.6 1.786 1.662 1.609 SiO ₂ / (Na ₂ O + B ₂ O ₃ ) 3.816 5.481 7.534 5.577 5.333 5.588 5.25 5.987 ( _Na2O + _Li2O )/ _SiO2 0.391 0.435 0.238 0.331 0.317 0.337 0.346 0.315 (ZrO ₂ +ZnO)/Na ₂ O 0.095 0.136 0.329 0.551 0.278 0.271 0.182 0.253 (P ₂ O ₅ +Na ₂ O)/Li ₂ O 1.837 1.08 2.052 1.712 1.887 1.813 2.014 1.729 (ZnO+RO+B ₂ O ₃ +TiO ₂ )/ P ₂ O ₅ 0.405 1 0.109 0.286 0 0 0 0.048 K ₂ O/ZrO ₂ 5.375 2 0.421 0.485 0.56 0.87 1.438 0.944 Crystalline Phase Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium Nephrite Grain size (nm) 30 25 30 26 28 27 twenty four 25 Fog (%) 0.10 0.08 0.10 0.10 0.05 0.06 0.08 0.07 Light transmittance at 550nm wavelength (%) 91.1 91.2 91.2 91.0 92.0 91.8 92.2 91.6 |B| value 0.5 0.5 0.9 0.8 0.5 0.6 0.4 0.5 H _v (kgf/mm ² ) 693 702 700 713 714 710 715 711 Body drop ball height (mm) 1300 1500 1600 1500 1600 1600 1500 1600

table 3. Example (wt%) 17# 18# 19# 20# twenty one# twenty two# twenty three# twenty four# SiO ₂ 49.7 48.5 44.8 46.9 49.8 48.9 46.4 51.5 Al ₂ O ₃ 28.1 27.6 28.5 28.3 27.4 26.5 25.6 25.4 _Li2O 6.8 9.2 8.1 7.3 6.5 7.4 9.4 7.6 _Na2O 8.2 7.5 9.3 9.7 10.4 8.6 10.2 7.7 _K2O 1.5 0.7 2.4 1 0.3 1.9 2.1 1.3 _{P2O5 ​} 3.4 5.3 4.5 4.8 3.6 3.3 2.2 4.1 ZrO ₂ 2 0.7 2.2 1.8 1.6 2.8 3.7 2.1 ZnO 0 0 0 0 0 0 0 0 _{B2O3 ​} 0 0 0 0 0 0 0 0 MgO 0 0 0 0 0 0 0 0 CaO 0 0 0 0 0 0 0 0 SrO 0 0 0 0 0 0 0 0 BaO 0 0 0 0 0 0 0 0 _TiO2 0 0 0 0 0 0 0 0 La ₂ O ₃ 0 0 0 0 0 0 0 0 _{Y2O3 ​} 0 0 0 0 0 0 0 0 _{Gd2O3 ​} 0 0 0 0 0 0 0 0 _{Sb2O3 ​} 0.3 0.5 0.2 0.2 0.4 0.6 0.4 0.3 _SnO2 0 0 0 0 0 0 0 0 SnO 0 0 0 0 0 0 0 0 _CeO2 0 0 0 0 0 0 0 0 Total 100 100 100 100 100 100 100 100 P ₂ O ₅ +ZrO ₂ 5.4 6 6.7 6.6 5.2 6.1 5.9 6.2 (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ 10.68 6.623 8.4 7.917 10.5 10.64 16.27 8.073 SiO ₂ /Al ₂ O ₃ 1.769 1.757 1.572 1.657 1.818 1.845 1.813 2.028 SiO ₂ / (Na ₂ O + B ₂ O ₃ ) 6.061 6.467 4.817 4.835 4.788 5.686 4.549 6.688 ( _Na2O + _Li2O )/ _SiO2 0.302 0.344 0.388 0.362 0.339 0.327 0.422 0.297 (ZrO ₂ +ZnO)/Na ₂ O 0.244 0.093 0.237 0.186 0.154 0.326 0.363 0.273 (P ₂ O ₅ +Na ₂ O)/Li ₂ O 1.706 1.391 1.704 1.986 2.154 1.608 1.319 1.553 (ZnO+RO+B ₂ O ₃ +TiO ₂ )/ P ₂ O ₅ 0 0 0 0 0 0 0 0 K ₂ O/ZrO ₂ 0.75 1 1.091 0.556 0.188 0.679 0.568 0.619 Crystalline Phase Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium nepheline, sodium nepheline Lithium Nephrite Lithium Nephrite Lithium Nephrite Grain size (nm) 26 30 25 26 28 25 twenty four 25 Fog (%) 0.05 0.09 0.08 0.05 0.08 0.06 0.05 0.06 Light transmittance at 550nm wavelength (%) 91.8 91.7 92.0 92.2 91.4 92.3 92.2 92.1 |B| value 0.5 0.4 0.6 0.5 0.5 0.6 0.4 0.5 H _v (kgf/mm ² ) 708 720 710 717 715 713 700 712 Body drop ball height (mm) 1500 1600 1600 1500 1600 1600 1400 1600

＜Glass-ceramic product example＞

This embodiment adopts the manufacturing method of the above-mentioned microcrystalline glass product to obtain microcrystalline glass products having the composition shown in Tables 4 to 6. In addition, the characteristics of each microcrystalline glass product are measured by the test method described in the present invention, and the measurement results are shown in Tables 4 to 6. In the following embodiments, the thickness of the test sample used for the four-point bending strength, drop ball test height, haze, light transmittance, |B| value, etc. is 0.7 mm.

Table 4. Example (wt%) 1# 2# 3# 4# 5# 6# 7# 8# SiO ₂ 48.3 49.4 42.5 47.8 52.9 45 41.1 43.3 Al ₂ O ₃ 22.5 24.6 34.3 23.2 25.3 35.2 20.5 21.8 _Li2O 5.2 3.7 6.5 13.4 4.5 2.5 12.4 10.3 _Na2O 11.3 12.4 5.6 4.3 6.6 7.2 15.1 13.7 _K2O 0.5 1.3 0.2 1.1 0.6 2.5 3.4 1.8 _{P2O5 ​} 6.2 5.4 8.5 2.8 1.5 4.3 3.8 5.2 ZrO ₂ 2.7 1.5 0.4 4.3 5.2 2.4 1.5 1.7 ZnO 2 0 0 0 0 0 0 0 _{B2O3 ​} 0 0 1.5 0 2 0 0.5 0 MgO 0 1 0 0 0 0.5 0 0 CaO 0 0 0 0.5 0 0 0 0 SrO 0 0 0 0 0 0 0 0 BaO 0 0 0 0 0 0 1.2 0.8 _TiO2 1 0.5 0 2 0 0 0 0 La ₂ O ₃ 0 0 0 0 0 0 0 1 _{Y2O3 ​} 0 0 0 0 1 0 0 0 _{Gd2O3 ​} 0 0 0 0 0 0 0 0 _{Sb2O3 ​} 0.3 0.2 0.5 0.6 0.4 0.3 0.5 0.4 _SnO2 0 0 0 0 0 0.1 0 0 SnO 0 0 0 0 0 0 0 0 _CeO2 0 0 0 0 0 0 0 0 Total 100 100 100 100 100 100 100 100 P ₂ O ₅ +ZrO ₂ 8.9 6.9 8.9 7.1 6.7 6.7 5.3 6.9 (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ 5.452 6.852 4.694 9.821 21.27 9.86 9.368 6.827 SiO ₂ /Al ₂ O ₃ 2.147 2.008 1.239 2.06 2.091 1.278 2.005 1.986 SiO ₂ / (Na ₂ O + B ₂ O ₃ ) 4.274 3.984 5.986 11.12 6.151 6.25 2.635 3.161 ( _Na2O + _Li2O )/ _SiO2 0.342 0.326 0.285 0.37 0.21 0.216 0.669 0.554 (ZrO ₂ +ZnO)/Na ₂ O 0.416 0.121 0.071 1 0.788 0.333 0.099 0.124 (P ₂ O ₅ +Na ₂ O)/Li ₂ O 3.365 4.811 2.169 0.53 1.8 4.6 1.524 1.835 (ZnO+RO+B ₂ O ₃ +TiO ₂ )/ P ₂ O ₅ 0.484 0.278 0.176 0.893 1.333 0.116 0.447 0.154 K ₂ O/ZrO ₂ 0.185 0.867 0.5 0.256 0.115 1.042 2.267 1.059 Crystalline Phase Lithium nepheline, sodium nepheline Sodium nepheline Lithium nepheline, sodium nepheline Lithium Nephrite Lithium nepheline, sodium nepheline Lithium nepheline, sodium nepheline Lithium nepheline, sodium nepheline Lithium nepheline, sodium nepheline Grain size (nm) 35 28 30 35 40 32 50 30 Fog (%) 0.10 0.10 0.08 0.13 0.14 0.09 0.12 0.08 Light transmittance at 550nm wavelength (%) 90.8 91.2 91.5 91.3 90.3 91.5 91.0 91.6 |B| value 1.0 1.1 0.9 0.9 0.7 1.2 0.7 0.6 Four-point bending strength (Mpa) 907 910 878 882 875 874 890 892 Depth of ion exchange layer (μm) 85 92 106 78 80 83 95 105 Drop ball test height (mm) 1500 1500 1400 1400 1400 1400 1500 1500 H _v (kgf/mm ² ) 805 820 812 830 796 803 813 824 Surface stress (Mpa) 184 192 188 175 170 193 180 185

table 5. Example (wt%) 9# 10# 11# 12# 13# 14# 15# 16# SiO ₂ 43.5 44.4 55 43.5 48 47.5 46.2 47.3 Al ₂ O ₃ 23.2 24.3 23.5 32.4 30 26.6 27.8 29.4 _Li2O 8.6 11.2 5.8 6.6 6.2 7.5 7.2 7 _Na2O 8.4 8.1 7.3 7.8 9 8.5 8.8 7.9 _K2O 4.3 2.2 0.8 1.6 1.4 2 2.3 1.7 _{P2O5 ​} 7.4 4 4.6 3.5 2.7 5.1 5.7 4.2 ZrO ₂ 0.8 1.1 1.9 3.3 2.5 2.3 1.6 1.8 ZnO 0 0 0.5 1 0 0 0 0.2 _{B2O3 ​} 3 0 0 0 0 0 0 0 MgO 0 0 0 0 0 0 0 0 CaO 0 0 0 0 0 0 0 0 SrO 0 0 0 0 0 0 0 0 BaO 0 1 0 0 0 0 0 0 _TiO2 0 3 0 0 0 0 0 0 La ₂ O ₃ 0 0 0 0 0 0 0 0 _{Y2O3 ​} 0.5 0 0 0 0 0 0 0 _{Gd2O3 ​} 0 0.5 0 0 0 0 0 0 _{Sb2O3 ​} 0.3 0.2 0.1 0 0.2 0.5 0.4 0.5 _SnO2 0 0 0.5 0.3 0 0 0 0 SnO 0 0 0 0 0 0 0 0 _CeO2 0 0 0 0 0 0 0 0 Total 100 100 100 100 100 100 100 100 P ₂ O ₅ +ZrO ₂ 8.2 5.1 6.5 6.8 5.2 7.4 7.3 6 (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ 4.27 8.1 6.696 11.49 14.44 6.882 6.421 8.881 SiO ₂ /Al ₂ O ₃ 1.875 1.827 2.34 1.343 1.6 1.786 1.662 1.609 SiO ₂ / (Na ₂ O + B ₂ O ₃ ) 3.816 5.481 7.534 5.577 5.333 5.588 5.25 5.987 ( _Na2O + _Li2O )/ _SiO2 0.391 0.435 0.238 0.331 0.317 0.337 0.346 0.315 (ZrO ₂ +ZnO)/Na ₂ O 0.095 0.136 0.329 0.551 0.278 0.271 0.182 0.253 (P ₂ O ₅ +Na ₂ O)/Li ₂ O 1.837 1.08 2.052 1.712 1.887 1.813 2.014 1.729 (ZnO+RO+B ₂ O ₃ +TiO ₂ )/ P ₂ O ₅ 0.405 1 0.109 0.286 0 0 0 0.048 K ₂ O/ZrO ₂ 5.375 2 0.421 0.485 0.56 0.87 1.438 0.944 Crystalline Phase Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium Nephrite Grain size (nm) 30 25 30 26 28 27 twenty four 25 Fog (%) 0.10 0.08 0.10 0.10 0.05 0.06 0.08 0.07 Light transmittance at 550nm wavelength (%) 91.1 91.2 91.2 91.0 92.0 91.8 92.2 91.6 |B| value 0.5 0.5 0.9 0.8 0.5 0.6 0.4 0.5 Four-point bending strength (Mpa) 895 913 902 896 922 930 915 917 Depth of ion exchange layer (μm) 107 125 118 130 120 116 126 121 Drop ball test height (mm) 1400 1700 1800 1600 1800 1800 1700 1800 H _v (kgf/mm ² ) 820 831 828 842 836 845 850 840 Surface stress (Mpa) 182 190 205 190 256 276 248 275

Table 6. Example (wt%) 17# 18# 19# 20# twenty one# twenty two# twenty three# twenty four# SiO ₂ 49.7 48.5 44.8 46.9 49.8 48.9 46.4 51.5 Al ₂ O ₃ 28.1 27.6 28.5 28.3 27.4 26.5 25.6 25.4 _Li2O 6.8 9.2 8.1 7.3 6.5 7.4 9.4 7.6 _Na2O 8.2 7.5 9.3 9.7 10.4 8.6 10.2 7.7 _K2O 1.5 0.7 2.4 1 0.3 1.9 2.1 1.3 _{P2O5 ​} 3.4 5.3 4.5 4.8 3.6 3.3 2.2 4.1 ZrO ₂ 2 0.7 2.2 1.8 1.6 2.8 3.7 2.1 ZnO 0 0 0 0 0 0 0 0 _{B2O3 ​} 0 0 0 0 0 0 0 0 MgO 0 0 0 0 0 0 0 0 CaO 0 0 0 0 0 0 0 0 SrO 0 0 0 0 0 0 0 0 BaO 0 0 0 0 0 0 0 0 _TiO2 0 0 0 0 0 0 0 0 La ₂ O ₃ 0 0 0 0 0 0 0 0 _{Y2O3 ​} 0 0 0 0 0 0 0 0 _{Gd2O3 ​} 0 0 0 0 0 0 0 0 _{Sb2O3 ​} 0.3 0.5 0.2 0.2 0.4 0.6 0.4 0.3 _SnO2 0 0 0 0 0 0 0 0 SnO 0 0 0 0 0 0 0 0 _CeO2 0 0 0 0 0 0 0 0 Total 100 100 100 100 100 100 100 100 P ₂ O ₅ +ZrO ₂ 5.4 6 6.7 6.6 5.2 6.1 5.9 6.2 (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ 10.68 6.623 8.4 7.917 10.5 10.64 16.27 8.073 SiO ₂ /Al ₂ O ₃ 1.769 1.757 1.572 1.657 1.818 1.845 1.813 2.028 SiO ₂ / (Na ₂ O + B ₂ O ₃ ) 6.061 6.467 4.817 4.835 4.788 5.686 4.549 6.688 ( _Na2O + _Li2O )/ _SiO2 0.302 0.344 0.388 0.362 0.339 0.327 0.422 0.297 (ZrO ₂ +ZnO)/Na ₂ O 0.244 0.093 0.237 0.186 0.154 0.326 0.363 0.273 (P ₂ O ₅ +Na ₂ O)/Li ₂ O 1.706 1.391 1.704 1.986 2.154 1.608 1.319 1.553 (ZnO+RO+B ₂ O ₃ +TiO ₂ )/ P ₂ O ₅ 0 0 0 0 0 0 0 0 K ₂ O/ZrO ₂ 0.75 1 1.091 0.556 0.188 0.679 0.568 0.619 Crystalline Phase Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium Nephrite Lithium nepheline, sodium nepheline Lithium Nephrite Lithium Nephrite Lithium Nephrite Grain size (nm) 26 30 25 26 28 25 twenty four 25 Fog (%) 0.05 0.09 0.08 0.05 0.08 0.06 0.05 0.06 Light transmittance at 550nm wavelength (%) 91.8 91.7 92.0 92.2 91.4 92.3 92.2 92.1 |B| value 0.5 0.4 0.6 0.5 0.5 0.6 0.4 0.5 Four-point bending strength (Mpa) 932 916 924 928 930 933 910 925 Depth of ion exchange layer (μm) 133 124 117 123 108 122 132 135 Drop ball test height (mm) 1700 1800 1800 1600 1800 1700 1500 1800 H _v (kgf/mm ² ) 822 855 834 838 841 842 830 850 Surface stress (Mpa) 264 258 277 261 274 280 275 254

It must be explained here that the above detailed description is only an implementation method provided to illustrate the technical content and features of the present invention. Any person with general knowledge in the field of the present invention, after understanding the technical content and features of the present invention, and without violating the spirit of the present invention, any simple modification, replacement or addition or reduction of components should fall within the scope of the patent application disclosed by the present invention.

without

without

Claims (73)

A microcrystalline glass product, the components of which are expressed by weight percentage, including: SiO ₂ : 40-60%; Al ₂ O ₃ : 20-40%; Li ₂ O: 2-15%; Na ₂ O: 3-20%; P ₂ O ₅ +ZrO ₂ : 1-15%. The microcrystalline glass product according to claim 1, further comprises, expressed in weight percentage, _K2O : 0-8%; and/or ZnO: 0-6%; and/or _B2O3 : 0-6%; and/or _RO : 0-8%; and/or _TiO2 : 0-5%; and/or _Ln2O3 : 0-5%; and/or _clarifier : 0-2%, wherein RO is one or more of MgO, CaO, SrO, and BaO _{, and Ln2O3} is one or more of _La2O3 , _{Gd2O3 , and Y2O3} . The glass-ceramic product according to claim 1 or 2, wherein the composition, expressed in weight percentage, satisfies one or more of the following eight conditions: 1) (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 3.0 to 30.0; 2) SiO ₂ /Al ₂ O ₃ is 1.2 to 2.8; 3) SiO ₂ /(Na ₂ O+B ₂ O ₃ ) is 2.0 to 15.0; 4) (Na ₂ O+Li ₂ O)/SiO ₂ is 0.1 to 0.8; 5) (ZrO ₂ +ZnO)/Na ₂ O is less than 2.0; 6) (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 0.5 to 8.0; 7) K ₂ O/ZrO ₂ is 0.1 or more; 8) (ZnO+RO+B ₂ O ₃ +TiO ₂ )/P ₂ O ₅ is less than 1.5, and the RO is one or more of MgO, CaO, SrO, and BaO. The glass-ceramic product according to claim 1 or 2, wherein the composition, expressed in weight percentage, satisfies one or more of the following eight conditions: 1) (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 4.0 to 20.0; 2) SiO ₂ /Al ₂ O ₃ is 1.3 to 2.5; 3) SiO ₂ /(Na ₂ O+B ₂ O ₃ ) is 3.0 to 10.0; 4) (Na ₂ O+Li ₂ O)/SiO ₂ is 0.15 to 0.7; 5) (ZrO ₂ +ZnO)/Na ₂ O is less than 1.5; 6) (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 0.8 to 5.0; 7) K ₂ O/ZrO ₂ is 0.2 to 10.0; 8) (ZnO+RO+B ₂ O ₃ +TiO ₂ )/ _P2O5 is less than _1.0 , and the RO is one or more of MgO, CaO, SrO, and BaO. The glass-ceramic product according to claim 1 or 2, wherein the composition, expressed in weight percentage, satisfies one or more of the following eight conditions: 1) (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 5.0-15.0; 2) SiO ₂ /Al ₂ O ₃ is 1.5-2.2; 3) SiO ₂ /(Na ₂ O+B ₂ O ₃ ) is 4.0-8.0; 4) (Na ₂ O+Li ₂ O)/SiO ₂ is 0.2-0.6; 5) (ZrO ₂ +ZnO)/Na ₂ O is 0.01-1.0; 6) (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 1.0-3.0; 7) K ₂ O/ZrO ₂ is 0.3-5.0; 8) (ZnO+RO+B ₂ O ₃ +TiO ₂ )/ _P2O5 is less than _0.5 , and the RO is one or more of MgO, CaO, SrO, and BaO. The glass-ceramic product according to claim 1 or 2, wherein the composition, expressed in weight percentage, satisfies one or more of the following eight conditions: 1) (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 6.0-10.0; 2) SiO ₂ /Al ₂ O ₃ is 1.6-2.0; 3) SiO ₂ /(Na ₂ O+B ₂ O ₃ ) is 5.0-7.0; 4) (Na ₂ O+Li ₂ O)/SiO ₂ is 0.25-0.5; 5) (ZrO ₂ +ZnO)/Na ₂ O is 0.1-0.5; 6) (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 1.5-2.5; 7) K ₂ O/ZrO ₂ is 0.4-1.5; 8) (ZnO+RO+B ₂ O ₃ +TiO ₂ )/ _P2O5 is less than _0.2 , and the RO is one or more of MgO, CaO, SrO, and BaO. The microcrystalline glass product according to claim 1 or 2, wherein the components are expressed in weight percentage, wherein: SiO ₂ : 43-55%; and/or Al ₂ O ₃ : 23-36%; and/or Li ₂ O: 3-13%; and/or Na ₂ O: 5-15%; and/or P ₂ O ₅ +ZrO ₂ : 2-12%; and/or K ₂ O: 0-5%; and/or ZnO: 0-3%; and/or B ₂ O ₃ : 0-3%; and/or RO: 0-5%; and/or TiO ₂ : 0-3%; and/or Ln ₂ O ₃ : 0-3%; and/or clarifier: 0-1%, wherein RO is one or more of MgO, CaO, SrO, and BaO, and Ln ₂ O ₃ is one or more of La ₂ O ₃ , Gd ₂ O ₃ , and Y ₂ O ₃ . The glass-ceramic product according to claim 1 or 2, wherein the components are expressed in weight percentage, wherein: SiO ₂ : 46-53%; and/or Al ₂ O ₃ : 25.5-32%; and/or Li ₂ O: 5.5-11%; and/or Na ₂ O: 6.5-12%; and/or P ₂ O ₅ +ZrO ₂ : 4-10%; and/or K ₂ O: 0.1-3%; and/or ZnO: 0-1%; and/or B ₂ O ₃ : 0-1%; and/or RO: 0-2%; and/or TiO ₂ : 0-1%; and/or Ln ₂ O ₃ : 0-1%; and/or clarifier: 0-0.5%, wherein RO is one or more of MgO, CaO, SrO, and BaO, and Ln ₂ O ₃ is La ₂ O ₃ , Gd ₂ O ₃ , Y ₂ O One or more of ₃ . The glass-ceramic product according to claim 1 or 2, wherein the components are expressed in weight percentage, wherein: ZrO ₂ : 0-5%; and/or P ₂ O ₅ : 1-8%. The glass-ceramic product according to any one of claims 1 to 3, wherein the components thereof are expressed in weight percentage, wherein: ZrO ₂ : 0.1 to 3%; and/or P ₂ O ₅ : 2 to 6%. The glass-ceramic product according to claim 1 or 2, further comprises, expressed in weight percentage, Yb ₂ O ₃ +Nb ₂ O ₅ +WO ₃ +Bi ₂ O ₃ +Ta ₂ O ₅ +TeO ₂ +GeO ₂ : 0-5%. According to the microcrystalline glass product described in claim 1 or 2, the main crystal phase of the microcrystalline glass product is the nepheline crystal phase, or the microcrystalline glass product only contains the nepheline crystal phase. According to the microcrystalline glass product described in claim 1 or 2, in the microcrystalline glass product, the weight percentage of the nepheline crystal phase in the microcrystalline glass product is 10 to 80%. According to the microcrystalline glass product described in claim 1 or 2, in the microcrystalline glass product, the weight percentage of the nepheline crystal phase in the microcrystalline glass product is 30-60%. According to the microcrystalline glass product described in claim 1 or 2, the ion exchange layer depth of the microcrystalline glass product is greater than 50μm; and/or the Vickers hardness is greater than 750kgf/ ^mm2 ; and/or the grain size is less than 80nm; and/or the surface stress is greater than 150MPa. According to the microcrystalline glass product described in claim 1 or 2, the ion exchange layer depth of the microcrystalline glass product is greater than 100μm; and/or the Vickers hardness is greater than 810kgf/ ^mm2 ; and/or the grain size is less than 40nm; and/or the surface stress is greater than 190MPa. The microcrystalline glass product described in claim 1 or 2 has a four-point bending strength of 700 MPa or more for a microcrystalline glass product with a thickness of less than 1 mm; and/or a drop ball test height of 1100 mm or more; and/or a haze of 0.15% or less; and/or a light transmittance of 550 nm wavelength of 88% or more; and/or an average light |B| value of 400 to 800 nm of less than 1.5. The microcrystalline glass product described in claim 1 or 2 has a four-point bending strength of 800 MPa or more for a microcrystalline glass product with a thickness of less than 1 mm; and/or a drop ball test height of 1500 mm or more; and/or a haze of 0.10% or less; and/or a light transmittance of 550 nm wavelength of 91% or more; and/or an average light |B| value of 400 to 800 nm of less than 0.8. According to the microcrystalline glass product described in claim 17, the thickness of the microcrystalline glass product is 0.2 to 1 mm. The glass-ceramic product according to claim 1 or 2, further comprises, expressed in weight percentage, the following components: NiO: 0-4%; and/or Ni ₂ O ₃ : 0-4%; and/or CoO: 0-2%; and/or Co ₂ O ₃ : 0-2%; and/or Fe ₂ O ₃ : 0-7%; and/or MnO ₂ : 0-4%; and/or Er ₂ O ₃ : 0-8%; and/or Nd ₂ O ₃ : 0-8%; and/or Cu ₂ O: 0-4%; and/or Pr ₂ O ₃ : 0-8%; and/or CeO ₂ : 0-4%. A glass-ceramic, the components of which are expressed by weight percentage: SiO ₂ : 40-60%; Al ₂ O ₃ : 20-40%; Li ₂ O: 2-15%; Na ₂ O: 3-20%; P ₂ O ₅ +ZrO ₂ : 1-15%. The glass-ceramics according to claim 21, further comprises, expressed in weight percentage, _K2O : 0-8%; and/or ZnO: 0-6%; and/or _B2O3 : 0-6%; and/or _RO : 0-8%; and/or _TiO2 : 0-5%; and/or _Ln2O3 : 0-5%; and/or clarifier: 0-2%, wherein RO is one or more of MgO, CaO _, SrO, and BaO, _{and Ln2O3} is one or _more of _{La2O3 , Gd2O3} , _{and Y2O3} . The glass-ceramics according to claim 21 or 22, wherein the composition, expressed in weight percentage, satisfies one or more of the following eight conditions: 1) (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 3.0 to 30.0; 2) SiO ₂ /Al ₂ O ₃ is 1.2 to 2.8; 3) SiO ₂ /(Na ₂ O+B ₂ O ₃ ) is 2.0 to 15.0; 4) (Na ₂ O+Li ₂ O)/SiO ₂ is 0.1 to 0.8; 5) (ZrO ₂ +ZnO)/Na ₂ O is 2.0 or less; 6) (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 0.5 to 8.0; 7) K ₂ O/ZrO ₂ is 0.1 or more; 8) (ZnO+RO+B ₂ O ₃ +TiO ₂ )/P ₂ O ₅ is less than 1.5, and the RO is one or more of MgO, CaO, SrO, and BaO. The glass-ceramics according to claim 21 or 22, wherein the composition, expressed in weight percentage, satisfies one or more of the following eight conditions: 1) (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 4.0 to 20.0; 2) SiO ₂ /Al ₂ O ₃ is 1.3 to 2.5; 3) SiO ₂ /(Na ₂ O+B ₂ O ₃ ) is 3.0 to 10.0; 4) (Na ₂ O+Li ₂ O)/SiO ₂ is 0.15 to 0.7; 5) (ZrO ₂ +ZnO)/Na ₂ O is less than 1.5; 6) (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 0.8 to 5.0; 7) K ₂ O/ZrO ₂ is 0.2 to 10.0; 8) (ZnO+RO+B ₂ O ₃ +TiO ₂ )/ _P2O5 is less than _1.0 , and the RO is one or more of MgO, CaO, SrO, and BaO. The glass-ceramics according to claim 21 or 22, wherein the composition, expressed in weight percentage, satisfies one or more of the following eight conditions: 1) (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 5.0-15.0; 2) SiO ₂ /Al ₂ O ₃ is 1.5-2.2; 3) SiO ₂ /(Na ₂ O+B ₂ O ₃ ) is 4.0-8.0; 4) (Na ₂ O+Li ₂ O)/SiO ₂ is 0.2-0.6; 5) (ZrO ₂ +ZnO)/Na ₂ O is 0.01-1.0; 6) (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 1.0-3.0; 7) K ₂ O/ZrO ₂ is 0.3-5.0; 8) (ZnO+RO+B ₂ O ₃ +TiO ₂ )/ _P2O5 is less than _0.5 , and the RO is one or more of MgO, CaO, SrO, and BaO. The glass-ceramics according to claim 21 or 22, wherein the composition, expressed in weight percentage, satisfies one or more of the following eight conditions: 1) (Al ₂ O ₃ +Na ₂ O)/P ₂ O ₅ is 6.0-10.0; 2) SiO ₂ /Al ₂ O ₃ is 1.6-2.0; 3) SiO ₂ /(Na ₂ O+B ₂ O ₃ ) is 5.0-7.0; 4) (Na ₂ O+Li ₂ O)/SiO ₂ is 0.25-0.5; 5) (ZrO ₂ +ZnO)/Na ₂ O is 0.1-0.5; 6) (P ₂ O ₅ +Na ₂ O)/Li ₂ O is 1.5-2.5; 7) K ₂ O/ZrO ₂ is 0.4-1.5; 8) (ZnO+RO+B ₂ O ₃ +TiO ₂ )/ _P2O5 is less than _0.2 , and the RO is one or more of MgO, CaO, SrO, and BaO. The glass-ceramics according to claim 21 or 22, wherein the components are expressed in weight percentage, wherein: SiO ₂ : 43-55%; and/or Al ₂ O ₃ : 23-36%; and/or Li ₂ O: 3-13%; and/or Na ₂ O: 5-15%; and/or P ₂ O ₅ +ZrO ₂ : 2-12%; and/or K ₂ O: 0-5%; and/or ZnO: 0-3%; and/or B ₂ O ₃ : 0-3%; and/or RO: 0-5%; and/or TiO ₂ : 0-3%; and/or Ln ₂ O ₃ : 0-3%; and/or clarifier: 0-1%, wherein RO is one or more of MgO, CaO, SrO, and BaO, and Ln ₂ O ₃ is one or more of La ₂ O ₃ , Gd ₂ O ₃ , and Y ₂ O ₃ . The glass-ceramics according to claim 21 or 22, wherein the components are expressed in weight percentage, wherein: SiO ₂ : 46-53%; and/or Al ₂ O ₃ : 25.5-32%; and/or Li ₂ O: 5.5-11%; and/or Na ₂ O: 6.5-12%; and/or P ₂ O ₅ +ZrO ₂ : 4-10%; and/or K ₂ O: 0.1-3%; and/or ZnO: 0-1%; and/or B ₂ O ₃ : 0-1%; and/or RO: 0-2%; and/or TiO ₂ : 0-1%; and/or Ln ₂ O ₃ : 0-1%; and/or clarifier: 0-0.5%, wherein RO is one or more of MgO, CaO, SrO, and BaO, and Ln ₂ O ₃ is La ₂ O ₃ , Gd ₂ O ₃ , Y ₂ O One or more of ₃ . The glass-ceramics according to claim 21 or 22, wherein the components are expressed in weight percentage, wherein: ZrO ₂ : 0-5%; and/or P ₂ O ₅ : 1-8%. The glass-ceramics according to claim 21 or 22, wherein the components are expressed in weight percentage, wherein: ZrO ₂ : 0.1-3%; and/or P ₂ O ₅ : 2-6%. The glass-ceramics according to claim 21 or 22, further comprises, expressed in weight percentage, the following components: Yb ₂ O ₃ +Nb ₂ O ₅ +WO ₃ +Bi ₂ O ₃ +Ta ₂ O ₅ +TeO ₂ +GeO ₂ : 0-5%. According to the microcrystalline glass described in claim 21 or 22, the main crystal phase of the microcrystalline glass is the nepheline crystal phase, or the microcrystalline glass only contains the nepheline crystal phase. According to the microcrystalline glass described in claim 21 or 22, in the microcrystalline glass, the weight percentage of the nepheline crystal phase in the microcrystalline glass is 10 to 80%. According to the microcrystalline glass described in claim 21 or 22, in the microcrystalline glass, the weight percentage of the nepheline crystal phase in the microcrystalline glass is 30 to 60%. The microcrystalline glass according to claim 21 or 22, wherein the grain size of the microcrystalline glass is less than 80 nm; and/or the Vickers hardness is greater than 650 kgf/mm ² . According to the microcrystalline glass described in claim 21 or 22, the grain size of the microcrystalline glass is less than 40nm; and/or the Vickers hardness is greater than 700kgf/ ^mm2 . According to the microcrystalline glass described in claim 21 or 22, the microcrystalline glass with a thickness of less than 1 mm has a body ball drop height of more than 1000 mm; and/or a haze of less than 0.15%; and/or a light transmittance of 550 nm wavelength of more than 88%; and/or an average light |B| value of 400 to 800 nm of less than 1.5. According to the microcrystalline glass described in claim 21 or 22, the microcrystalline glass with a thickness of less than 1 mm has a body ball drop height of more than 1400 mm; and/or a haze of less than 0.10%; and/or a light transmittance of 550 nm wavelength of more than 91%; and/or an average light |B| value of 400 to 800 nm of less than 0.8. According to the microcrystalline glass described in claim 37, the thickness of the microcrystalline glass is 0.2 to 1 mm. The glass-ceramics according to claim 21 or 22, further comprises, expressed in weight percentage, the following components: NiO: 0-4%; and/or Ni ₂ O ₃ : 0-4%; and/or CoO: 0-2%; and/or Co ₂ O ₃ : 0-2%; and/or Fe ₂ O ₃ : 0-7%; and/or MnO ₂ : 0-4%; and/or Er ₂ O ₃ : 0-8%; and/or Nd ₂ O ₃ : 0-8%; and/or Cu ₂ O: 0-4%; and/or Pr ₂ O ₃ : 0-8%; and/or CeO ₂ : 0-4%. A matrix glass, the components of which are expressed by weight percentage, include: SiO ₂ : 40-60%; Al ₂ O ₃ : 20-40%; Li ₂ O: 2-15%; Na ₂ O: 3-20%; P ₂ O ₅ +ZrO ₂ : 1-15%. The base glass according to claim 41, further comprises, expressed in weight percentage, _K2O : 0-8%; and/or ZnO: 0-6%; and/or _B2O3 : 0-6%; and/or _RO : 0-8%; and/or _TiO2 : 0-5%; and/or _Ln2O3 : 0-5%; and/or _clarifier : 0-2%, wherein RO is one or more of MgO, CaO, SrO, and BaO, _{and Ln2O3 is} one or _more of _La2O3 , _Gd2O3 , _{and Y2O3} . The matrix glass _according to claim ₄₁ or 42, wherein the composition is expressed in weight percentage, wherein: ( _Al2O3 + _Na2O )/ _P2O5 is 3.0-30.0; and/or _SiO2 / _Al2O3 is 1.2-2.8; and/or _SiO2 /( _Na2O + _{B2O3 )} is 2.0-15.0; and/or ( _Na2O + _Li2O )/ _SiO2 is 0.1-0.8; and/or ( _ZrO2 + _ZnO )/ _Na2O is 2.0 or less; and/or ( _P2O5 + _Na2O )/ _Li2O is 0.5-8.0; and/or _K2O / _ZrO2 is 0.1 or more; and/or (ZnO+ _RO + _B2O3 + _TiO2 )/ _P2O3 is 0.1 or more _{. 5} is less than 1.5, and the RO is one or more of MgO, CaO, SrO, and BaO. The matrix glass _according to claim ₄₁ or 42, wherein the composition is expressed in weight percentage, wherein: ( _Al2O3 + _Na2O )/ _P2O5 is 4.0-20.0; and/or _SiO2 / _Al2O3 is 1.3-2.5; and/or _SiO2 /( _Na2O + _{B2O3 )} is 3.0-10.0; and/or ( _Na2O + _Li2O )/ _SiO2 is 0.15-0.7; and/or ( _ZrO2 + _ZnO )/ _Na2O is 1.5 or less; and/or ( _P2O5 + _Na2O )/ _Li2O is _0.8-5.0 ; and/or _K2O / _ZrO2 is 0.2-10.0; and/or (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O3 is ₀ . ₅ is less than 1.0, and the RO is one or more of MgO, CaO, SrO, and BaO. The matrix glass _according to claim ₄₁ or 42, wherein the composition is expressed in weight percentage, wherein: ( _Al2O3 + _Na2O )/ _P2O5 is 5.0-15.0; and/or _SiO2 / _Al2O3 is 1.5-2.2; and/or _SiO2 /( _Na2O + _{B2O3 )} is 4.0-8.0; and/or ( _Na2O + _Li2O )/ _SiO2 is 0.2-0.6; and/or ( _ZrO2 + _ZnO )/ _Na2O is 0.01-1.0; and/or ( _P2O5 + _Na2O )/ _Li2O is 1.0-3.0; and/or _K2O /ZrO2 is 0.3-5.0; and/or (ZnO+ _RO + _B2O3 +TiO2)/ _{P2O3 is} 1.5-2.2; and/or (ZnO+RO+ _B2O3 + _TiO2 )/ ₅ is less than 0.5, and the RO is one or more of MgO, CaO, SrO, and BaO. The matrix glass according to claim ₄₁ or 42, wherein the composition is expressed in weight percentage, wherein: ( _Al2O3 + _Na2O )/ _P2O5 is _6.0-10.0 ; and/or _SiO2 / _Al2O3 is 1.6-2.0; and/or _SiO2 /( _Na2O + _{B2O3 )} is 5.0-7.0; and/or ( _Na2O + _Li2O )/ _SiO2 is 0.25-0.5; and/or ( _ZrO2 + _ZnO )/ _Na2O is 0.1-0.5; and/or ( _P2O5 + _Na2O )/ _Li2O is 1.5-2.5; and/or _K2O / _ZrO2 is 0.4-1.5; and/or (ZnO+RO+ _B2O3 + _TiO2 )/ _P2O3 is _{0 . 5} is less than 0.2, and the RO is one or more of MgO, CaO, SrO, and BaO. The base glass according to claim 41 or 42, wherein the components are expressed in weight percentage, wherein: SiO ₂ : 43-55%; and/or Al ₂ O ₃ : 23-36%; and/or Li ₂ O: 3-13%; and/or Na ₂ O: 5-15%; and/or P ₂ O ₅ +ZrO ₂ : 2-12%; and/or K ₂ O: 0-5%; and/or ZnO: 0-3%; and/or B ₂ O ₃ : 0-3%; and/or RO: 0-5%; and/or TiO ₂ : 0-3%; and/or Ln ₂ O ₃ : 0-3%; and/or fining agent: 0-1%, wherein RO is one or more of MgO, CaO, SrO, and BaO, and Ln ₂ O ₃ is one or more of La ₂ O ₃ , Gd ₂ O ₃ , and Y ₂ O ₃ . The matrix glass according to claim 41 or 42, wherein the components are expressed in weight percentage, wherein: SiO ₂ : 46-53%; and/or Al ₂ O ₃ : 25.5-32%; and/or Li ₂ O: 5.5-11%; and/or Na ₂ O: 6.5-12%; and/or P ₂ O ₅ +ZrO ₂ : 4-10%; and/or K ₂ O: 0.1-3%; and/or ZnO: 0-1%; and/or B ₂ O ₃ : 0-1%; and/or RO: 0-2%; and/or TiO ₂ : 0-1%; and/or Ln ₂ O ₃ : 0-1%; and/or fining agent: 0-0.5%, wherein RO is one or more of MgO, CaO, SrO, and BaO, and Ln ₂ O ₃ is La ₂ O ₃ , Gd ₂ O ₃ , Y ₂ O One or more of ₃ . The matrix glass according to claim 41 or 42, wherein the components thereof are expressed in weight percentage, wherein: ZrO ₂ : 0-5%; and/or P ₂ O ₅ : 1-8%. The matrix glass according to claim 41 or 42, wherein the components thereof are expressed in weight percentage, wherein: ZrO ₂ : 0.1-3%; and/or P ₂ O ₅ : 2-6%. The base glass according to claim 41 or 42, further comprising, expressed in weight percentage, Yb ₂ O ₃ +Nb ₂ O ₅ +WO ₃ +Bi ₂ O ₃ +Ta ₂ O ₅ +TeO ₂ +GeO ₂ : 0-5%; and/or NiO: 0-4%; and/or Ni ₂ O ₃ : 0-4%; and/or CoO: 0-2%; and/or Co ₂ O ₃ : 0-2%; and/or Fe ₂ O ₃ : 0-7%; and/or MnO ₂ : 0-4%; and/or Er ₂ O ₃ : 0-8%; and/or Nd ₂ O ₃ : 0-8%; and/or Cu ₂ O: 0-4%; and/or Pr ₂ O ₃ : 0-8%; and/or CeO ₂ : 0-4%. A glass-ceramic formed body comprising the glass-ceramic described in any one of claims 21 to 40. A glass cover comprises the microcrystalline glass product described in any one of claims 1 to 20, and/or the microcrystalline glass described in any one of claims 21 to 40, and/or the base glass described in any one of claims 41 to 51, and/or the microcrystalline glass formed body described in claim 52. A glass component comprises the microcrystalline glass product described in any one of claims 1 to 20, and/or the microcrystalline glass described in any one of claims 21 to 40, and/or the base glass described in any one of claims 41 to 51, and/or the microcrystalline glass formed body described in claim 52. A display device comprises the microcrystalline glass product described in any one of claims 1 to 20, and/or the microcrystalline glass described in any one of claims 21 to 40, and/or the base glass described in any one of claims 41 to 51, and/or the microcrystalline glass formed body described in claim 52, and/or the glass cover plate described in claim 53, and/or the glass component described in claim 54. An electronic device comprises the microcrystalline glass product described in any one of claims 1 to 20, and/or the microcrystalline glass described in any one of claims 21 to 40, and/or the base glass described in any one of claims 41 to 51, and/or the microcrystalline glass formed body described in claim 52, and/or the glass cover plate described in claim 53, and/or the glass component described in claim 54. A method for manufacturing a glass-ceramic product according to any one of claims 1 to 20, the method comprising the following steps: forming a base glass, subjecting the base glass to a crystallization process to form a glass-ceramic, and then subjecting the glass-ceramic to a chemical strengthening process to form a glass-ceramic product. According to the manufacturing method of the microcrystalline glass product described in claim 57, the crystallization process includes the following steps: heating to a specified crystallization treatment temperature, maintaining the temperature for a certain period of time after reaching the crystallization treatment temperature, and then cooling down, the crystallization treatment temperature is 580-750°C, and the holding time at the crystallization treatment temperature is 0-8 hours. According to the manufacturing method of the microcrystalline glass product described in claim 57, the crystallization process includes the following steps: heating to a specified crystallization treatment temperature, maintaining the temperature for a certain time after reaching the crystallization treatment temperature, and then cooling down, the crystallization treatment temperature is 600-700°C, and the holding time at the crystallization treatment temperature is 1-6 hours. According to the method for manufacturing a microcrystalline glass product as described in claim 57, the crystallization process includes the following steps: performing a nucleation process at a first temperature, and then performing a crystal growth process at a second temperature higher than the nucleation process temperature. According to the manufacturing method of the microcrystalline glass product described in claim 60, the crystallization process includes the following steps: the first temperature is 500-620°C, the second temperature is 620-750°C; the holding time at the first temperature is 0-24 hours; and the holding time at the second temperature is 0-10 hours. According to the manufacturing method of the microcrystalline glass product described in claim 57, the crystallization process includes the following steps: the first temperature is 500-620°C, the second temperature is 620-750°C; the holding time at the first temperature is 2-15 hours; the holding time at the second temperature is 0.5-6 hours. According to the manufacturing method of the microcrystalline glass product described in any one of claims 57 to 62, the chemical strengthening process includes: immersing the microcrystalline glass in a salt bath of molten Na salt at a temperature of 350 to 470°C for 1 to 36 hours; and/or immersing the microcrystalline glass in a salt bath of molten K salt at a temperature of 360 to 450°C for 1 to 36 hours; and/or immersing the microcrystalline glass in a mixed salt bath of molten K salt and Na salt at a temperature of 360 to 450°C for 1 to 36 hours. According to the manufacturing method of the microcrystalline glass product described in any one of claims 57 to 62, the chemical strengthening process includes: immersing the microcrystalline glass in a salt bath of molten Na salt at a temperature of 380 to 460°C for 2 to 10 hours; and/or immersing the microcrystalline glass in a salt bath of molten K salt at a temperature of 360 to 450°C for 1 to 10 hours; and/or immersing the microcrystalline glass in a mixed salt bath of molten K salt and Na salt at a temperature of 360 to 450°C for 2 to 24 hours. A method for manufacturing microcrystalline glass according to any one of claims 21 to 40, the method comprising the following steps: forming a matrix glass, and then forming microcrystalline glass through a crystallization process of the matrix glass. According to the method for manufacturing microcrystalline glass as described in claim 65, the crystallization process includes the following steps: heating to a specified crystallization treatment temperature, maintaining the temperature for a certain period of time after reaching the crystallization treatment temperature, and then cooling down, the crystallization treatment temperature is 580 to 750°C, and the holding time at the crystallization treatment temperature is 0 to 8 hours. According to the method for manufacturing microcrystalline glass as described in claim 65, the crystallization process includes the following steps: heating to a specified crystallization treatment temperature, maintaining the temperature for a certain period of time after reaching the crystallization treatment temperature, and then cooling down, the crystallization treatment temperature is 600-700°C, and the holding time at the crystallization treatment temperature is 1-6 hours. According to the method for manufacturing microcrystalline glass as described in claim 65, the crystallization process includes the following steps: performing a nucleation process at a first temperature, and then performing a crystal growth process at a second temperature higher than the nucleation process temperature. According to the method for manufacturing microcrystalline glass as described in claim 65, the crystallization process includes the following steps: the first temperature is 500-620°C, the second temperature is 620-750°C; the holding time at the first temperature is 0-24 hours; and the holding time at the second temperature is 0-10 hours. According to the method for manufacturing microcrystalline glass as described in claim 65, the crystallization process includes the following steps: the first temperature is 500-620°C, the second temperature is 620-750°C; the holding time at the first temperature is 2-15 hours; and the holding time at the second temperature is 0.5-6 hours. A method for manufacturing a microcrystalline glass formed body according to claim 52, the method comprising grinding or polishing the microcrystalline glass to form a microcrystalline glass formed body, or subjecting base glass or microcrystalline glass to a hot bending process or a pressing process at a certain temperature to form a microcrystalline glass formed body. A method for manufacturing a microcrystalline glass formed body according to claim 52, the method comprising the following steps: subjecting the base glass to a primary crystallization heat treatment process, including heating, heat preservation for nucleation, heating, heat preservation for crystallization, and cooling to room temperature to form pre-crystallized glass; and heat-processing the pre-crystallized glass to obtain a microcrystalline glass formed body. A method for manufacturing a microcrystalline glass formed body according to claim 52, the method comprising the following steps: 1) Heating and preheating: placing the base glass or pre-crystallized glass or microcrystalline glass in a mold, the mold passes through each heating station in the heat bending machine in turn, and stays at each station for a certain period of time to keep warm, the temperature of the preheating zone is 400-800°C, the pressure is 0.01-0.05MPa, and the time is 40-200s; 2) Pressurized molding: after preheating, the mold is transferred to the molding station, the heat bending machine applies a certain pressure to the mold, the pressure range is 0.1-0.8Mpa, the molding station temperature range is 650-850°C, and the molding time range is 40-200s; 3) Pressure-maintaining cooling: The mold is transferred to the cooling station for cooling step by step. The cooling temperature range is 750-500℃, the pressure is 0.01-0.05Mpa, and the time is 40-200s.