US20120052271A1 - Two-step method for strengthening glass - Google Patents

Two-step method for strengthening glass Download PDF

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US20120052271A1
US20120052271A1 US13/211,661 US201113211661A US2012052271A1 US 20120052271 A1 US20120052271 A1 US 20120052271A1 US 201113211661 A US201113211661 A US 201113211661A US 2012052271 A1 US2012052271 A1 US 2012052271A1
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glass
mol
cations
layer
depth
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Sinue Gomez
Lisa Ann Lamberson
Robert Michael Morena
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Corning Inc
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Corning Inc
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Priority to US13/211,661 priority Critical patent/US20120052271A1/en
Assigned to CORNING INCORPORATED reassignment CORNING INCORPORATED ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: LAMBERSON, LISA ANN, MORENA, ROBERT MICHAEL, GOMEZ, SINUE
Publication of US20120052271A1 publication Critical patent/US20120052271A1/en
Priority to US14/504,755 priority patent/US10227253B2/en
Priority to US16/295,685 priority patent/US11078106B2/en
Abandoned legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C21/00—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C21/00—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface
    • C03C21/001—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface in liquid phase, e.g. molten salts, solutions
    • C03C21/002—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface in liquid phase, e.g. molten salts, solutions to perform ion-exchange between alkali ions
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/089—Glass compositions containing silica with 40% to 90% silica, by weight containing boron
    • C03C3/091—Glass compositions containing silica with 40% to 90% silica, by weight containing boron containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/095—Glass compositions containing silica with 40% to 90% silica, by weight containing rare earths
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/097—Glass compositions containing silica with 40% to 90% silica, by weight containing phosphorus, niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C4/00—Compositions for glass with special properties
    • C03C4/18—Compositions for glass with special properties for ion-sensitive glass
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C2204/00—Glasses, glazes or enamels with special properties
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/24—Structurally defined web or sheet [e.g., overall dimension, etc.]
    • Y10T428/24942—Structurally defined web or sheet [e.g., overall dimension, etc.] including components having same physical characteristic in differing degree
    • Y10T428/2495—Thickness [relative or absolute]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/31—Surface property or characteristic of web, sheet or block
    • Y10T428/315—Surface modified glass [e.g., tempered, strengthened, etc.]

Definitions

  • the disclosure relates to strengthened alkali aluminoborosilicate glasses. More particularly, the disclosure relates to a method of strengthening such glasses. Even more particularly, the disclosure relates to strengthening such glasses by ion exchange.
  • the ion exchange process can be used to strengthen alkali-containing glasses by creating compressive stress layers in the surface region of the glass.
  • lithium-containing aluminosilicate glasses are ion exchanged more readily than sodium-containing glasses and greater depths of compression can be obtained in lithium-containing aluminosilicate glasses at lower temperatures and shorter times.
  • such lithium-containing aluminosilicate glasses tend to have lower strain and anneal points, and lower temperatures are required for treatment to avoid structural relaxation.
  • the exchange of sodium for lithium in the glass results in lower surface compression—which translates into lower surface strength—when compared to the surface compression achieved with the exchange of potassium for sodium in the glass.
  • a method of strengthening an alkali aluminoborosilicate glass is provided.
  • a compressive layer extending from a surface of the glass to a depth of layer is formed by exchanging larger metal cations for smaller metal cations present in the glass.
  • metal cations in the glass are exchanged for larger metal cations to a second depth that is less than the depth of layer.
  • the second step increases the compressive stress of the compressive layer. For example, sodium cations are exchanged in the first step for lithium cations that are present in the glass to the depth of layer, and potassium cations are then exchanged in the second step for sodium cations and lithium cations in the glass to the second depth.
  • the exchange of the potassium cations for sodium and lithium cations increases the compressive stress of the layer. Formation of the compressive layer and replacement of cations with larger cations can be achieved by a two-step ion exchange process.
  • An alkali aluminoborosilicate glass having a compressive layer and a crack indentation threshold of at least 3000 gf is also provided.
  • one aspect of the disclosure is to provide a method of strengthening an alkali aluminoborosilicate glass.
  • the method comprises the steps of: providing an alkali aluminoborosilicate glass comprising alkali metal cations; forming a compressive layer extending from a surface of the glass to a depth of layer, wherein the compressive layer is under a compressive stress; and replacing at least a portion of the alkali metal cations with a larger alkali metal cation to a second depth that is less than the depth of layer, and wherein replacing the alkali metal cations with the larger alkali metal cation increases the compressive stress.
  • a second aspect of the disclosure is to provide a method of strengthening an alkali aluminoborosilicate glass.
  • the method comprises the steps of: providing the alkali aluminoborosilicate glass comprising lithium cations and sodium cations; replacing at least a portion of the lithium cations with sodium cations to form a compressive layer that extends from a surface of the glass to a depth of layer and is under compressive stress; and replacing at least a portion of the sodium cations and the lithium cations with potassium cations to a second depth that is less than the depth of layer, wherein the compressive layer is enriched in potassium cations to the second depth, and wherein replacing sodium cations and lithium cations with potassium cations increases the compressive stress of the compressive layer.
  • a third aspect of the disclosure is to provide an alkali aluminoborosilicate glass.
  • the glass comprises lithium cations, sodium cations, and potassium cations.
  • the glass has a surface having a compressive layer extending from the surface to a depth of layer and is enriched in potassium cations to a second depth that is less than the depth of layer.
  • the surface of the glass has a crack initiation threshold of at least 3000 gf upon indentation with a Vickers indenter.
  • FIG. 1 is a schematic cross-sectional view of a glass sheet, described herein, having strengthened surfaces
  • FIG. 2 is a plot of crack initiation loads obtained for alkali aluminoborosilicate glasses measured before strengthening and following strengthening by ion exchange processes;
  • FIG. 3 a is plot of Na 2 O concentration profile following the first step of a two-step ion exchange process.
  • FIG. 3 b is plot of K 2 O concentration profile following the second step of a two-step ion exchange process.
  • the term “enriched,” unless otherwise specified, means that the concentration of a specified element or ionic specie is greater than the average concentration of that element or ionic specie within the bulk of the glass.
  • glass refers to alkali aluminoborosilicate glasses, unless otherwise specified.
  • the method comprises the steps of: providing the alkali aluminoborosilicate glass; initially forming a compressive layer extending from a surface of the glass to a depth of layer; and replacing at least a portion of alkali metal cations with a larger alkali metal cation to a second depth that is less than the depth of layer. Replacing the alkali metal cations with the larger alkali metal cation increases the compressive stress in the compressive layer and increases the damage resistance of the surface of the glass.
  • the compressive layer inhibits the introduction of flaws at the surface and prevents crack initiation and propagation through the depth of the layer.
  • the method is carried out through the use of a two-step ion exchange process.
  • an alkali aluminoborosilicate glass is provided.
  • the glass is provided in the form of a sheet having a thickness of about 2 mm or less.
  • Such sheets can be formed by down-draw methods known in the art such as slot-draw or fusion-draw processes, or by other methods known in the art.
  • the glass in some embodiments, comprises monovalent lithium cations, and sodium cations.
  • the glass can additionally include monovalent potassium cations.
  • the presence of such alkali metal cations in the glass is typically represented by the oxide species Li 2 O, Na 2 O, and K 2 O.
  • the alkali aluminoborosilicate glass comprises, consists essentially of, or consists of: 50-70 mol % SiO 2 ; 5-15 mol % Al 2 O 3 ; 5-20 mol % B 2 O 3 ; 2-15 mol % Li 2 O; 0-20 mol % Na 2 O; and 0-10 mol % K 2 O.
  • the glass can further comprise at least one of: 0-10 mol % P 2 O 5 ; 0-5 mol % MgO; 0-1 mol % CeO 2 ; and 0-1 mol % SnO 2 .
  • Non-limiting compositions and physical properties of representative glasses are listed in Table 1.
  • Crack initiation thresholds which were determined by indentation with a Vickers indenter, are also listed for the compositions in Table 1.
  • the alkali aluminoborosilicate glass as provided has intrinsically high damage resistance; i.e., the glass has high damage resistance prior to—or without—any chemical or thermal strengthening or tempering. Such damage resistance is measured or characterized by the resistance of the glass to crack formation and/or crack propagation upon indentation with a Vickers indenter.
  • the glass has a crack initiation threshold (i.e., the Vickers indenter load at which cracks are first observed) of at least about 1000 gf before strengthening and, in particular embodiments, in a range from about 1000 gf up to about 2000 gf, prior to strengthening. Examples of glass compositions that intrinsically have crack initiation thresholds in this range are listed in Table 2.
  • soda-lime glasses have low damage tolerance, and form cracks when indented at loads as low as 100 gf. Even when ion-exchanged, soda-lime glass typically has a damage tolerance of less than 1000 gf.
  • the formation of the compressive layer and increase damage resistance described herein can, in some embodiments, be achieved by a two-step ion exchange process.
  • ions in the surface layer of the glass are replaced by—or exchanged with—larger ions having the same valence or oxidation state as the ions present in the glass.
  • the exchange of metal cations is typically carried out in a molten salt bath, with larger cations from the bath typically replacing smaller cations within the glass.
  • Ion exchange is limited to a region extending from the surface of the glass article to a depth (depth of layer, or “DOL”) below the surface.
  • ion exchange of alkali metal-containing glasses can be achieved by immersing the glass in at least one molten salt bath containing a salt such as, but not limited to, nitrates, sulfates, and chlorides of at least one alkali metal ion.
  • a salt such as, but not limited to, nitrates, sulfates, and chlorides of at least one alkali metal ion.
  • the temperature of such molten salt baths is typically in a range from about 380° C. up to about 450° C., with immersion times ranging up to about 16 hours. However, temperatures and immersion times that are different from those described herein can also be used.
  • the replacement or exchange of smaller cations within the glass with larger cations from the bath creates a compressive stress in the region near the surface of the glass to the depth of layer. The compressive stress near the surface gives rise to a central tension in an inner or central region of the glass so as to balance forces within the glass.
  • the step of initially forming the compressive layer provides a compressive layer having an unusually deep depth of layer.
  • the step of forming the compressive layer comprises replacing smaller alkali metal cations with larger alkali metal cations.
  • this step comprises replacing lithium cations in the glass with sodium cations from, for example, a molten salt bath, by ion exchange to the depth of layer below the surface of the glass.
  • the exchange of Na + ions for Li + ions achieves an advantageously deep depth of layer (e.g., d 1 , d 2 , in FIG. 1 ).
  • the depth of layer is at least 50 ⁇ m, and can, in some embodiments, extend from the surface to a depth in a range from about 70 ⁇ m up to about 290 ⁇ m.
  • the exchange of Na + ions for Li + ions can be achieved by immersing the glass in a first ion exchange bath comprising at least one molten sodium salt.
  • the sodium salt is sodium nitrate (NaNO 3 ).
  • the ion exchange bath contains only sodium salt; i.e., no other metal salts are intentionally added to the bath.
  • the first ion exchange bath further includes salts of other alkali metals such as, but not limited to, potassium nitrate (KNO 3 ).
  • the first ion exchange bath comprises 40% NaNO 3 and 60% KNO 3 by weight.
  • the first ion exchange bath comprises 20% NaNO 3 and 80% KNO 3 by weight.
  • the small alkali metal cations (e.g., Li + , Na + ) in the compressive layer are replaced by a single, larger alkali metal cation specie to a second depth (e.g., d 1 ′, d 2 ′, in FIG. 1 ) that is less than the depth of layer.
  • this is achieved by exchanging potassium ions for at least one of sodium ions and lithium ions in the glass.
  • the exchange of K + ions for Na + ions and Li + to the second depth increases the surface compressive stress of the glass.
  • the second depth extends from the surface to a depth in a range from about 5 ⁇ m up to about 20 ⁇ m.
  • Such ion exchange is achieved by immersing the glass in a second ion exchange bath comprising a potassium sodium salt.
  • the potassium salt is potassium nitrate (KNO 3 ).
  • the glass After the glass has been strengthened by forming the deep compressive layer and replacing smaller ions with larger ions to a lesser depth using the two-step ion exchange process described hereinabove, the glass has a crack initiation threshold of at least 3000 gf when indented with a Vickers indenter, a compressive stress of at least 500 MPa, and a depth of layer of at least 50 ⁇ m.
  • An alkali aluminoborosilicate glass comprising lithium cations, sodium cations, and potassium cations is also provided.
  • the glass has a compressive stress layer extending from a surface of the glass to a depth of layer.
  • the compressive layer of the glass is enriched in potassium cations to a second depth that is less than the depth of layer.
  • the surface also has a crack initiation threshold of at least 3000 gf when indented with a Vickers indenter.
  • strengthened glass sheet 100 has a thickness t, a first surface 110 and second surface 120 that are substantially parallel to each other, central portion 115 .
  • Compressive layers 112 , 122 extend from first surface 110 and second surface 120 , respectively, to depths of layer d 1 , d 2 , below each surface.
  • Compressive layers 112 , 122 are under a compressive stress, while central portion 115 is under a tensile stress, or in tension.
  • the tensile stress in central portion 115 balances the compressive stresses in compressive layers 112 , 122 , thus maintaining equilibrium within strengthened glass sheet 100 .
  • Each of compressive layers 112 , 122 of the glass is enriched in potassium cations to second depths d 1 ′, d 2 ′, respectively, wherein second depths d 1 ′, d 2 ′ are less than depths of layer d 1 , d 2 .
  • a glass sheet having compressive layers 112 , 122 extending from opposite surfaces 120 , 120 is shown in FIG. 1
  • the glass described herein can have a strengthened single surface, rather than multiple strengthened surfaces. This can be achieved, for example, by masking one of surfaces 110 , 120 during the two-step ion exchange process, which is described herein and is used to strengthen glass sheet 100 .
  • the first depth of layer extends from the surface of the glass to a depth in a range from about 70 ⁇ m up to about 290 ⁇ m.
  • the second depths d 1 ′, d 2 ′ extend from surfaces 112 , 122 to a depth in a range from about 5 ⁇ m up to about 20 ⁇ m.
  • the compressive layer is, in some embodiments, formed by the methods described hereinabove, such as, for example, the two-step ion exchange process described above.
  • the method comprises the steps of: providing the alkali aluminoborosilicate glass; forming a compressive layer extending from a surface of the glass to a depth of layer (d 1 , d 2 in FIG. 1 ); wherein the compressive layer is under a compressive stress; and replacing alkali metal cations in the compressive layer with a larger alkali metal cation to a second depth (d 1 ′, d 2 ′ in FIG. 1 ) that is less the depth of layer.
  • the replacement of the alkali metal cations with a larger alkali metal cationic specie increases the compressive stress in the compressive layer.
  • the glass is in the form of a sheet having a thickness of about 2 mm or less. Such sheets can be formed by down-draw methods known in the art such as slot-draw or fusion-draw processes, or by other methods known in the art.
  • the alkali aluminoborosilicate glass comprises, consists essentially of, or consists of: 50-70 mol % SiO 2 ; 5-15 mol % Al 2 O 3 ; 5-20 mol % B 2 O 3 ; 2-15 mol % Li 2 O; 0-20 mol % Na 2 O; and 0-10 mol % K 2 O.
  • the glass can further comprise at least one of: 0-10 mol % P 2 O 5 ; 0-5 mol % MgO; 0-1 mol % CeO 2 ; and 0-1 mol % SnO 2 .
  • Compositions and physical properties, and damage resistance of representative glasses are listed in Table 1.
  • the glasses described herein intrinsically (i.e., prior to thermal or chemical strengthening (e.g., ion exchange)) possess high levels of damage resistance. Such damage resistance is measured or characterized by the resistance of the glass to crack formation and/or crack propagation upon indentation with a Vickers indenter.
  • the glass has a crack initiation threshold (i.e., the Vickers indenter load at which cracks are first observed) of at least about 1000 gf before strengthening and, in particular embodiments, in a range from about 1000 gf up to about 2000 gf, prior to strengthening. Examples of glass compositions that intrinsically have crack initiation thresholds in this range are listed in Table 2.
  • soda-lime glasses have low damage tolerance, and form cracks when indented at loads as low as 100 gf. Even when ion-exchanged, soda-lime glass typically has a damage tolerance of less than 1000 gf.
  • the tolerance to damage and strength of the alkali aluminoborosilicate glasses having intrinsic damage resistance can be greatly enhanced by the use of a 2 step ion-exchange process.
  • the two-step strengthening/ion exchange processes described hereinabove provide new opportunities for the use of such glasses in those consumer electronics applications where high strength and scratch resistance are desirable.
  • Such applications include, but are not limited to, cover plates, display windows, display screens, touch screens, and the like for portable or hand-held electronic communication and entertainment devices.
  • Glass samples having selected compositions were subjected to single-step ion exchange by immersion in a single molten salt bath.
  • Different glass samples having these same compositions were subjected to two-step ion exchange in multiple salt baths, in accordance with the methods described hereinabove.
  • the single-step ion exchange baths used were: a) a 390° C. molten NaNO 3 salt bath; and b) a 390° C. molten salt bath containing 60% KNO 3 and 40% NaNO 3 by weight.
  • the glass samples that were ion exchanged in the pure NaNO 3 bath were immersed in the bath for 5 hours. Glass samples that were ion exchanged in the KNO 3 /NaNO 3 bath were immersed in the bath for 10 hours.
  • the first set of multiple baths consisted of a first bath of molten NaNO 3 salt at 390° C., followed by a second bath of molten KNO 3 salt at 390° C. Glass samples were immersed in the first (NaNO 3 ) bath for 10 hours, and then immersed in the second (KNO 3 ) bath for 30 minutes.
  • the second set of multiple baths consisted of a first bath of molten NaNO 3 salt at 410° C., followed by a second bath of molten KNO 3 salt at 410° C. Glass samples were immersed in the first (NaNO 3 ) bath for 10 hours, and then immersed in the second (KNO 3 ) bath for 10 minutes.
  • crack initiation thresholds for soda lime glass were measured before ion exchange and after ion exchange in a 410° C. KNO 3 bath for 8 hours.
  • Table 3 lists depths of layer (DOL) and compressive stresses (CS) measured for 1 mm alkali aluminoborosilicate glass samples following different ion exchange (IX) procedures.
  • the compositions of the samples listed in Table 3 are: i) 65.7 mol % SiO 2 ; 12.3 mol % Al 2 O 3 ; 9.1 mol % B 2 O 3 ; 5 mol % Li 2 O; 6 . 6 mol % Na 2 O; 1 . 3 mol % K 2 O; 0 .
  • One set of samples of each composition was ion exchanged in a single-step process by immersion in a 390° C. molten salt bath containing 80 wt % KNO 3 and 20 wt % NaNO 3 for 5 hours.
  • Two-step ion exchange consisted of immersion a 390° C. molten salt bath containing 80 wt % KNO 3 and 20 wt % NaNO 3 for 5 hours followed by immersion in a 410° C. KNO 3 molten salt bath for 1 hour.
  • Immersion in the second ion exchange bath in accordance with the methods described hereinabove increased the compressive stress of all samples.
  • a second set of samples of each composition was ion exchanged in a single-step process by immersion in a 390° C. molten salt bath containing 60 wt % KNO 3 and 40 wt % NaNO 3 for 5 hours.
  • Two-step ion exchange consisted of immersion a 390° C. molten salt bath containing 60 wt % KNO 3 and 40 wt % NaNO 3 for 5 hours followed by immersion in a 410° C. KNO 3 molten salt bath for 1 hour.
  • Immersion in the second ion exchange bath in accordance with the methods described hereinabove increased the compressive stress of all samples.
  • Two-step 791 711 726 1) 80 wt % KNO 3 /20 wt % NaNO 3 ; 5 hrs at 390° C.; 2) KNO 3 ; 1 hr at 410° C.
  • the strengths of alkali aluminoborosilicate glass samples before ion exchange and after single-step and two-step ion exchange processes were also measured using ring-on-ring measurements performed on polished surfaces of 1 mm thick glass samples. All samples comprised 65.7 mol % SiO 2 ; 10.3 mol % Al 2 O 3 ; 12.1 mol % B 2 O 3 ; 4.6 mol % Li 2 O; 6.2 mol % Na 2 O; and 1.1 mol % K 2 O. The measured ring-on-ring strength of the sample before ion exchange was 131 ⁇ 45 MPa. Single-step ion exchange in a 390° C.
  • molten salt bath containing 60 wt % KNO 3 and 40 wt % NaNO 3 for 6 hours yielded a ring-on-ring strength of 491 ⁇ 108 MPa.
  • Two-step ion exchange consisted of immersion in a 390° C. molten salt bath containing 60 wt % KNO 3 and 40 wt % NaNO 3 for 6 hours followed by immersion in a 410° C. KNO 3 molten salt bath for 1 hour yielded a ring-on-ring strength of 647 ⁇ 215 MPa.
  • the two-step ion exchange process in accordance with the methods described hereinabove, thus resulted in an increase in ring-on-ring strength of about 30% over the single-step process.
  • FIG. 3 a is a plot of the Na 2 O concentration profile determined by electron microprobe analysis following the first ion exchange step (immersion in a 390° C. molten NaNO 3 salt bath for 5 hours).
  • FIG. 3 b is a plot of the K 2 O concentration profile determined by electron microprobe analysis following the second ion exchange step (immersion in a 410° C.
  • molten KNO 3 salt bath for: a) 0 minutes (i.e., corresponding to single-step ion exchange); b) 10 minutes; c) 20 minutes; and d) 60 minutes.
  • the concentrations of Na + and K + ions correspond to the Na 2 O and K 2 O concentrations, respectively, shown in FIGS. 3 a and 3 b .
  • the K + and Na + concentrations on the glass surface relate to compressive stress, while the distance these ions diffuse into the glass relates to the depth of layer of the compressive layer.
  • the first step of the two-step process develops the deep depth of layer, while the second step ( FIG.

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US11078106B2 (en) 2021-08-03
JP2018104284A (ja) 2018-07-05
JP2020100558A (ja) 2020-07-02
EP2609047A1 (fr) 2013-07-03
CN111908806A (zh) 2020-11-10
WO2012027660A1 (fr) 2012-03-01
KR20130135841A (ko) 2013-12-11
CN103068759A (zh) 2013-04-24
US20150030840A1 (en) 2015-01-29
KR20190077605A (ko) 2019-07-03
JP6301984B2 (ja) 2018-03-28
US10227253B2 (en) 2019-03-12
EP3517511A1 (fr) 2019-07-31
KR102408475B1 (ko) 2022-06-14
KR20210021405A (ko) 2021-02-25
US20190202730A1 (en) 2019-07-04
TW201217283A (en) 2012-05-01
JP2013536155A (ja) 2013-09-19
EP2609047B1 (fr) 2019-03-20
JP6883131B2 (ja) 2021-06-09
JP6732823B2 (ja) 2020-07-29
JP5890835B2 (ja) 2016-03-22
JP2016084282A (ja) 2016-05-19
KR101995081B1 (ko) 2019-07-01

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