Li2O—Al2O3—SiO2 based crystallized glass and method for producing same

Abstract

In a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass using SnO.sub.2 as a substitute fining agent for As.sub.2O.sub.3 or Sb.sub.2O.sub.3, a crystallized glass having less yellow coloration is provided at low costs. The glass is a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass comprising from 0.01 to 0.9% of SnO.sub.2 in terms of % by mass and having a content of each of As.sub.2O.sub.3 and Sb.sub.2O.sub.3 of 1,000 ppm or less as a glass composition, which has a V.sub.2O.sub.5 content of from 0.08 to 15 ppm in the glass composition.

Claims

1. A method for producing a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass, which comprises preparing a raw material batch so as to form a glass comprising from 0.01 to 0.9% of SnO.sub.2 in terms of % by mass and having a content of each of As.sub.2O.sub.3 and Sb.sub.2O.sub.3 of 1,000 ppm or less, melting and forming the batch to produce a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallizable glass, and subsequently subjecting the glass to a heat treatment to achieve crystallization, wherein the b* value of L*a*b* colorimetric system of CIE standard of the crystallized glass standard is from 0 to 4.5 at a thickness of 3 mm and wherein selection of raw materials and management of steps are performed so that a V.sub.2O.sub.5 content in the crystallized glass becomes from 0.08 to 15 ppm.

2. The method for producing a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass according to claim 1, which comprises preparing the batch so as to form a glass comprising from 55 to 75% of SiO.sub.2, from 10 to 35% of Al.sub.2O.sub.3, from 1 to 10% of Li.sub.2O, from 0.2 to 5% of MgO, from 0 to 5% of ZnO, from 0 to 10% of BaO, from 0 to 4% of TiO.sub.2, from 0 to 5% of ZrO.sub.2, from 0 to 4% of P.sub.2O.sub.5, and from 0.01 to 0.9% of SnO.sub.2, in terms of % by mass, as a glass composition.

3. The method for producing a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass according to claim 2, wherein a raw material having a V.sub.2O.sub.5 content of 50 ppm or less is used as a raw material of Al.sub.2O.sub.3.

4. The method for producing a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass according to claim 2, wherein a raw material having a V.sub.2O.sub.5 content of 400 ppm or less is used as a raw material of MgO.

5. The method for producing a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass according to claim 2, wherein the batch is prepared so as to form a glass comprising from 17 to 27% of Al.sub.2O.sub.3 and from 0.2 to 4% of MgO, in terms of % by mass, as a glass composition.

6. The method for producing a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass according to claim 1, wherein melting is performed at a temperature of less than 1,750 C.

7. The method for producing a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass according to claim 1, wherein a -quartz solid solution is precipitated as a main crystal by a heat treatment.

Description

EMBODIMENTS FOR CARRYING OUT THE INVENTION

(1) The following will describe the Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass of the present invention. Incidentally, the term % in the following explanation means % by mass unless otherwise indicated.

(2) In the Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass of the present invention, the V.sub.2O.sub.5 content is strictly restricted and is reduced to a level where the coloring of V.sub.2O.sub.5 does not cause an influence. The reason why the coloring of V.sub.2O.sub.5 becomes not problematic in the case of using As.sub.2O.sub.3 or Sb.sub.2O.sub.3 and becomes problematic in the case of using SnO.sub.2 is not sufficiently elucidated but the present inventors have surmised as follows.

(3) V.sub.2O.sub.5 and SnO.sub.2 are not incorporated into a crystal and remain in a glass matrix phase. In other words, these components are concentrated in the glass matrix phase. Furthermore, when an oxidation-reduction reaction with V.sub.2O.sub.5 from standard electrode potential is compared, in SnO.sub.2, the oxidation reaction from Sn.sup.2+ to Sn.sup.4+ is energetically advantageous and V.sub.2O.sub.5 is liable to be reduced, thereby increasing V.sup.4+. In combination of these conditions, even when the content of V.sub.2O.sub.5 is minute, it is considered that the coloration of the glass becomes a non-negligible level. On the other hand, in As.sub.2O.sub.3 or Sb.sub.2O.sub.3, when the oxidation-reduction reaction with V.sub.2O.sub.5 from standard electrode potential is compared as described above, the reduction reaction of V.sub.2O.sub.5 becomes energetically disadvantageous as compared with the case of SnO.sub.2 and thus V.sub.2O.sub.5 is difficultly reduced, so that V.sup.4+ is not increased. Accordingly, in the conventional crystallized glass using As.sub.2O.sub.3 or Sb.sub.2O.sub.3 as a fining agent, it is considered that the coloration by V.sub.2O.sub.5 does not become problematic.

(4) The following will describe a mixing source of V.sub.2O.sub.5. As the mixing of V.sub.2O.sub.5, mixing from the raw materials and mixing at the glass production process are considered.

(5) First, the mixing of V.sub.2O.sub.5 from the glass raw materials will be described. When impurities contained in glass raw materials are analyzed, it has been confirmed that there are raw materials containing much V.sub.2O.sub.5 as an impurity among those widely used as raw materials of Al.sub.2O.sub.3 and MgO. Moreover, there exist those containing a large amount of V.sub.2O.sub.5 also among the other raw materials, for example, those to be used as raw materials of SiO.sub.2, raw materials of ZrO.sub.2, and the like. Therefore, it is desirable to select raw materials each containing less amount of the V.sub.2O.sub.5 impurity, especially raw materials of Al.sub.2O.sub.3 and MgO each having a small content of V.sub.2O.sub.5. Moreover, it is desirable to design a composition having small contents of Al.sub.2O.sub.3 and MgO so that the use amounts of the raw materials of Al.sub.2O.sub.3 and MgO can be reduced as far as possible.

(6) The following will describe the mixing of V.sub.2O.sub.5 from the glass production process. In the case where a glass using V.sub.2O.sub.5 as a raw material is produced in the same factory or a glass containing V.sub.2O.sub.5 is stored in the factory, a raw material of V.sub.2O.sub.5 or a cullet of a glass containing V.sub.2O.sub.5 is easily mixed in at a conveying line of the raw material or the cullet. In such a case, it is desirable to reduce V.sub.2O.sub.5 to be mixed in from the process as far as possible by no use of the line in which the raw material of V.sub.2O.sub.5 is handled at the time of conveying raw materials or batch blending or by keeping the conveying line and a storage place of the V.sub.2O.sub.5-containing glass cullet away from the production line of the Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass as far as possible.

(7) In the Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass of the present invention, the V.sub.2O.sub.5 content is limited to from 0.08 to 15 ppm. As already mentioned, the V.sub.2O.sub.5 amount of 15 ppm or less can be achieved by devising raw materials, a glass composition, steps, and the like. When V.sub.2O.sub.5 is controlled to 15 ppm or less, a less colored Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass, especially a transparent Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass can be obtained. The content of V.sub.2O.sub.5 is preferably 10 ppm or less, more preferably 5 ppm or less, and further preferably 3 ppm or less.

(8) Incidentally, even when complete prevention of the mixing of V.sub.2O.sub.5 from the process is succeeded, it is difficult to prevent the mixing of V.sub.2O.sub.5 from raw materials completely. When raw materials resulting in the V.sub.2O.sub.5 amount of 0.08 ppm or less are used, costs for the raw material drastically increase, so that it becomes difficult to obtain an inexpensive Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass. Accordingly, when the V.sub.2O.sub.5 content is defined to 0.08 ppm or more, preferably 0.1 ppm or more, further preferably 0.3 ppm or more, it becomes possible to provide a lower-cost and inexpensive Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass.

(9) As.sub.2O.sub.3 or Sb.sub.2O.sub.3 are environmental burden substances and are not substantially contained in the present invention. Specifically, the content of each of As.sub.2O.sub.3 and Sb.sub.2O.sub.3 is 1,000 ppm or less, preferably 500 ppm or less, and further preferably 200 ppm or less.

(10) SnO.sub.2 is a component to be a substitute fining agent for As.sub.2O.sub.3 or Sb.sub.2O.sub.3. The content of SnO.sub.2 is 0.01% or more, preferably 0.08% or more, and especially preferably 0.1% or more. An upper limit of the content of SnO.sub.2 is 0.9%, more preferably 0.5% or less, more preferably 0.4% or less, and especially preferably 0.3% or less. When the content of SnO.sub.2 is less than 0.01%, the effect as a fining agent is difficultly obtained. On the other hand, when the content of SiO.sub.2 exceeds 0.9%, the coloration of V.sub.2O.sub.5 as a minute component becomes strong or the coloration of TiO.sub.2 and Fe.sub.2O.sub.3 becomes too strong, so that the crystallized glass is liable to be colored yellowish and is prone to be easily devitrified.

(11) Also, the Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass of the present invention preferably comprises a composition of from 55 to 75% of SiO.sub.2, from 10 to 35% of Al.sub.2O.sub.3, from 1 to 10% of Li.sub.2O, from 0.2 to 5% of MgO, from 0 to 5% of ZnO, from 0 to 10% of BaO, from 0 to 4% of TiO.sub.2, from 0 to 5% of ZrO.sub.2, from 0 to 4% of P.sub.2O.sub.5, and from 0.01 to 0.9% of SnO.sub.2, in terms of % by mass. Particularly, the glass desirably comprises a composition of from 60 to 75% of SiO.sub.2, from 17 to 27% of Al.sub.2O.sub.3, from 3 to 6% of Li.sub.2O, from 0.2 to 4% of MgO, from 0 to 4% of ZnO, 3.7Li.sub.2O+0.741MgO+0.367ZnO5.0, from 0.3 to 10% of BaO, from 0 to 2% of TiO.sub.2, from 1 to 4% of ZrO.sub.2, from 1 to 6% of TiO.sub.2+ZrO.sub.2, from 0 to 3% of P.sub.2O.sub.5, and from 0.01 to 0.3% of SnO.sub.2, in terms of % by mass. The following will describe reasons why each component is defined as described above.

(12) SiO.sub.2 is a component that forms a skeleton of the glass and also constitutes a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystal. The content of SiO.sub.2 is preferably from 55 to 75%, more preferably from 58 to 70%, and especially preferably from 60 to 68%. When the content of SiO.sub.2 is too small, the coefficient of thermal expansion tends to become high and it becomes difficult to obtain a crystallized glass excellent in thermal impact resistance. Also, chemical durability tends to decrease. On the other hand, when the content of SiO.sub.2 is too large, melting ability of the glass becomes worse and the viscosity of a glass melt increases, so that there is a tendency that fining becomes difficult and forming of the glass becomes difficult.

(13) Al.sub.2O.sub.3 is a component that forms a skeleton of the glass and also constitutes a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystal. Moreover, Al.sub.2O.sub.3 can reduce, by its presence in the remaining glass phase of the crystallized glass, an increase in coloration due to SnO.sub.2 and thus can diminish the coloration of the Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass to be a base. The larger the Al.sub.2O.sub.3 content in the glass composition is, the more the Al.sub.2O.sub.3 amount in the remaining glass phase after crystallization is, so that the coloration of the base glass can be reduced. Therefore, the content of Al.sub.2O.sub.3 is preferably 10% or more, more preferably 17% or more, further preferably 20% or more, especially preferably 20.5% or more, and most preferably 21.0% or more. When the content of Al.sub.2O.sub.3 is small, there is a tendency that the effect of reducing the increase in the coloration due to SnO.sub.2 becomes difficult to obtain. Also, the coefficient of thermal expansion tends to become high and it becomes difficult to obtain a crystallized glass excellent in thermal impact resistance. Also, chemical durability tends to decrease. On the other hand, raw materials of Al.sub.2O.sub.3 frequently contain much V.sub.2O.sub.5 impurity. Moreover, when the content of Al.sub.2O.sub.3 is too large, melting ability of the glass becomes worse and the viscosity of a glass melt increases, so that there is a tendency that fining becomes difficult and forming of the glass becomes difficult. Furthermore, crystals of mullite precipitate and the glass tends to devitrify. Accordingly, an upper limit of the content of Al.sub.2O.sub.3 is preferably 35% or less, more preferably 30% or less, further preferably 27% or less, and especially preferably 25% or less.

(14) Li.sub.2O is a component that constitutes a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystal, and is a component that exerts a large influence on crystallinity and also lowers the viscosity of the glass to improve glass melting ability and forming ability. The content of Li.sub.2O is preferably 1% or more, more preferably 2% or more, further preferably 2.5% or more, and especially preferably 3% or more. When the content of Li.sub.2O is too small, crystals of mullite precipitate and the glass tends to devitrify. Also, at the time of crystallization of the glass, the Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystal is less liable to precipitate and there is a tendency that a crystallized glass excellent in thermal impact resistance is difficult to obtain. Furthermore, melting ability of the glass becomes worse and the viscosity of a glass melt increases, so that there is a tendency that fining becomes difficult and forming of the glass becomes difficult. On the other hand, when the content of Li.sub.2O is too large, the crystallinity becomes too strong, so that the glass tends to devitrify and the glass is liable to break. Accordingly, the content of Li.sub.2O is preferably 10% or less, more preferably 6% or less, further preferably 5% or less, and especially preferably 4.5% or less, and most preferably 4% or less.

(15) MgO is a component that exerts an influence on the coefficient of thermal expansion. For example, in the case where the glass is used in heat-resistant applications, in order to reduce a risk of breakage by thermal impact, the coefficient of thermal expansion is preferably close to 0 as far as possible. Accordingly, in the crystallized glass of the present invention, it is preferable that MgO is contained in an amount of 0.2% or more, particularly 0.5% or more. When MgO is contained in an amount of 0.2% or more, the coefficient of thermal expansion of the crystallized glass is liable to be close to 0. On the other hand, since a raw material of MgO tends to contain much V.sub.2O.sub.5 impurity, the mixing amount of V.sub.2O.sub.5 is liable to increase when the content of MgO is too large. Accordingly, the content of MgO is preferably 5% or less and more preferably 4% or less, and it is particularly preferable to limit the content to 2.9% or less.

(16) ZnO is a component that exerts an influence on the coefficient of thermal expansion and its content is preferably from 0 to 5%, more preferably from 0 to 4%, and especially preferably from 0 to 3%. When the content of ZnO is too large, devitrification is liable to occur.

(17) Furthermore, it is preferable to limit Li.sub.2O+0.741MgO+0.367ZnO to 5.0% or less, particularly 4.8% or less, 4.6% or less, further 4.5% or less. When the value is small, the Al.sub.2O.sub.3 amount in the remaining glass phase in the crystallized glass is liable to be large and the coloration of the crystallized glass to be a base may be easily reduced. On the other hand, when the value of the above formula is too small, a grain diameter of the Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystal in the crystallized glass becomes large and there is a tendency that white turbidity is liable to generate. As a result, there is a concern that a transparent feeling of the crystallized glass is impaired, so that a lower limit thereof is preferably set to 3.7% or more.

(18) BaO is a component that enhances a fining effect and, in the case of obtaining a white opaque glass, enhances whiteness of the glass. Its content is preferably from 0 to 10% and especially preferably from 0.3 to 10%. When the content of BaO is too large, the coefficient of thermal expansion tends to become large.

(19) TiO.sub.2 and ZrO.sub.2 are nucleation agents. The contents of these nucleation agents are desirably strictly controlled for the following reasons. Namely, the larger the content of TiO.sub.2 is, the more the crystal nuclei form and the less liable the generation of white turbidity is. On the other hand, when the content of TiO.sub.2 is large, the coloration is liable to be strong. Moreover, the larger the content of ZrO.sub.2 is, the more the crystal nuclei form and the less liable the generation of white turbidity is. On the other hand, when the content of ZrO.sub.2 is large, devitrification tendency becomes strong and there is a tendency that a problem tends to occur in the forming step. Accordingly, an appropriate range of these nucleation agents are investigated in consideration of the Al.sub.2O.sub.3 amount, the amount of Li.sub.2O+0.741MgO+0.367ZnO, and the like. As a result, the content of TiO.sub.2 is preferably from 0 to 4%, more preferably from 1 to 3.5%, and especially preferably from 1 to 2.8% and the content of ZnO.sub.2 is preferably from 0 to 5% and especially preferably from 1 to 4%. A lower limit of TiO.sub.2+ZrO.sub.2 (total amount of TiO.sub.2 and ZrO.sub.2) is preferably 1% and especially preferably 3%. Moreover, an upper limit of TiO.sub.2+ZrO.sub.2 is preferably 9% and particularly desirably 6%.

(20) P.sub.2O.sub.5 is a component that promotes phase separation of the glass and makes the precipitation of the Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystal easy. Its content is preferably from 0 to 4% and particularly desirably from 0 to 3%. When the content of P.sub.2O.sub.5 is too large, white turbidity is liable to generate and the coefficient of thermal expansion tends to increase.

(21) When Nd.sub.2O.sub.3 and CoO that are colorants are used, the coloration can be reduced due to the effect of complementary colors. However, Nd.sub.2O.sub.3 and CoO are rare resources and cost high, so that it becomes difficult to provide a low-cost and inexpensive Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass when these components are used. Moreover, transmittance in a visible region is lowered and the appearance looks blackish, and a transparent feeling tends to be impaired. Therefore, the contents of Nd.sub.2O.sub.3 and CoO are preferably each less than 500 ppm, more preferably each less than 300 ppm, and further desirably each less than 100 ppm.

(22) Also, as for Fe.sub.2O.sub.3 that mixes in as an impurity component, the content is desirably limited. Specifically, the content of Fe.sub.2O.sub.3 is preferably 250 ppm or less and especially preferably 200 ppm or less. As for Fe.sub.2O.sub.3, a smaller content is more preferable, since coloration decreases. However, for example, in order to control the content to less than 50 ppm, it is necessary to use highly pure raw materials and it becomes difficult to provide an inexpensive Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass. Accordingly, the content of Fe.sub.2O.sub.3 is desirably 50 ppm or more.

(23) In addition, in the Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass of the present invention, color tone of a transmitted light at a thickness of 3 mm is preferably 4.5 or less, more preferably 4.0 or less, and especially preferably 3.5 or less in terms of the b* value of L*a*b* indication of CIE standard. Also, transmittance of a light having a wavelength of 525 nm is preferably 89% or more and especially preferably 89.5% or more at a thickness of 1.1 mm.

(24) Furthermore, since the Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass of the present invention is used in heat-resistance applications, the coefficient of thermal expansion is preferably close to zero as far as possible. Specifically, the coefficient is preferably from 2.510.sup.7/ C. to 2.510.sup.7/ C. and especially preferably from 1.510.sup.7/ C. to 1.510.sup.7/ C. in a temperature range of from 30 to 380 C. When the coefficient of thermal expansion is out of the range, a risk of breakage by thermal impact is liable to increase.

(25) The following will describe the method for producing a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass of the present invention.

(26) First, a batch is prepared so as to be a target glass composition. Since the target composition is as already described, an explanation thereof is omitted.

(27) Here, it is necessary to select a raw material of Al.sub.2O.sub.3, a raw material of MgO, and the like each having a small V.sub.2O.sub.5 content so that the V.sub.2O.sub.5 amount contained in a glass becomes from 0.08 to 15 ppm. In addition, contamination with V.sub.2O.sub.5 from the process is excluded as far as possible by managing the steps. For example, dedicated equipments are used for compounding and conveying a raw material batch and a place of installing a line is devised so that no influence is exerted from production facilities of a V.sub.2O.sub.5 containing glass.

(28) Then, the glass raw material batch is melted. A degree of the coloration of the crystallized glass is influenced by not only the glass composition but also melting conditions. Particularly, in the case of adding SnO.sub.2, the coloration tends to become strong when the molten glass goes toward a reduction direction. The reason is considered that Sn.sup.2+ has a large influence on the coloration as compared with Sn.sup.4+. In order that the molten glass may not go toward the reduction direction as far as possible, it is preferable that melting temperature is lowered or melting time is shortened. For the melting time, melting efficiency (melting area/flow rate) can be adopted as its index. Thus, by limiting the melting temperature and the melting efficiency, it becomes possible to prevent the molten glass from going toward the reduction direction to obtain a crystallized glass having a reduced coloration.

(29) Maximum temperature at the time of glass melting is preferably less than 1,750 C. and especially preferably 1,700 C. or less. When the maximum temperature at the time of glass melting is 1,750 C. or more, a component of Sn is liable to be reduced and the coloration tends to become strong. The phenomenon tends to occur more remarkably particularly when V.sub.2O.sub.5 is present as an impurity. A lower limit of the maximum temperature at the time of glass melting is not particularly limited but is preferably 1,600 C. or more and especially preferably 1,650 C. or more in order to advance a glass reaction sufficiently to obtain a homogeneous glass.

(30) The melting efficiency of the glass is preferably from 1 to 6 m.sup.2/(t/day), and especially preferably from 1.5 to 5 m.sup.2/(t/day). When the melting efficiency of the glass is less than 1 m.sup.2/(t/day), the melting time is shortened and as a result fining time is also shortened, so that there is a tendency that a glass excellent in bubble quality is difficult to obtain. On the other hand, when the melting efficiency of the glass exceeds 6 m.sup.2/(t/day), a component of Sn is liable to be reduced and the coloration tends to become strong.

(31) Subsequently, by forming the molten glass into a predetermined shape, a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallizable glass can be obtained. Here, as a forming method, various forming methods such as a float method, a press method, a roll-out method, and an overflow method can be applied depending on an objective shape.

(32) Thereafter, the formed Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallizable glass was subjected to a heat treatment at from 600 to 800 C. for from 1 to 5 hours to form crystal nuclei (crystal nuclei-forming stage) and further subjected to a heat treatment at from 800 to 950 C. for from 0.5 to 3 hours to precipitate a Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystal as a main crystal (crystal-growing stage), thereby obtaining a transparent crystallized glass containing a -quartz solid solution (Li.sub.2O.Al.sub.2O.sub.3.nSiO.sub.2 [4>n2]) as a main crystal. Incidentally, when the Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallizable glass is subjected to a heat treatment at from 600 to 800 C. for from 1 to 5 hours to form crystal nuclei and then further subjected to a heat treatment at from 1,050 to 1,250 C. for from 0.5 to 3 hours, a white crystallized glass containing a 3-spodumene solid solution (Li.sub.2O.Al.sub.2O.sub.3.nSiO.sub.2 [n4]) as a main crystal can be also obtained.

(33) The thus prepared Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass of the present invention is provided for various applications after being subjected to post processing such as cutting, polishing, or bending processing, or being subjected to decoration on the surface.

EXAMPLES

(34) The present invention is hereunder described with reference to Examples but the present invention should not be construed as being limited to the following Examples.

(35) TABLE-US-00001 TABLE 1 Glass composition Sample No. (% by mass) 1 2 3 4 5 6 SiO.sub.2 65.5 65.4 65.6 65.5 65.2 65.5 Al.sub.2O.sub.3 22.3 22.2 22.4 22.4 21.9 22.3 Li.sub.2O 3.7 3.7 3.7 3.7 4.2 3.7 Na.sub.2O 0.4 0.4 0.4 0.4 0.4 0.4 K.sub.2O 0.3 0.3 0.3 0.3 0.3 0.3 MgO 0.7 0.7 0.7 0.7 0.9 0.7 ZnO BaO 1.2 1.2 1.2 1.2 1.2 1.2 TiO.sub.2 2.0 2.0 2.0 2.0 2.0 2.0 ZrO.sub.2 2.2 2.2 2.2 2.2 2.2 2.2 P.sub.2O.sub.5 1.4 1.4 1.4 1.4 1.4 1.4 SnO.sub.2 0.3 0.5 0.1 0.2 0.3 0.3 Fe.sub.2O.sub.3 (ppm) 100 100 100 100 100 100 V.sub.2O.sub.5 (ppm) 2 1 3 0.3 3 2 Nd.sub.2O.sub.3 Li + 0.741Mg + 0.367Zn 4.2 4.2 4.2 4.2 4.9 4.2 Melting temperature ( C.) 1680 1680 1680 1680 1680 1750 Color tone b* 3.0 2.9 3.2 2.5 2.5 3.8 Transmittance (%) 89.9 89.9 89.9 90.2 89.8 89.2 Coefficient of thermal expansion 0.9 0.9 0.9 0.9 1.1 0.9 (10.sup.7/ C.)

(36) TABLE-US-00002 TABLE 2 Glass composition Sample No. (% by mass) 7 8 9 10 11 SiO.sub.2 65.5 65.2 65.2 65.2 65.2 Al.sub.2O.sub.3 22.3 21.9 22.3 21.9 21.9 Li.sub.2O 3.7 3.7 3.7 4.2 4.2 Na.sub.2O 0.4 0.4 0.4 0.4 0.4 K.sub.2O 0.3 0.3 0.3 0.3 0.3 MgO 0.7 0.7 0.7 0.9 0.9 ZnO BaO 1.2 1.2 1.2 1.2 1.2 TiO.sub.2 2.0 2.0 2.0 2.0 2.0 ZrO.sub.2 2.2 2.2 2.2 2.2 2.2 P.sub.2O.sub.5 1.4 1.4 1.4 1.4 1.4 SnO.sub.2 0.3 1.0 0.3 Fe.sub.2O.sub.3 (ppm) 100 100 100 100 100 V.sub.2O.sub.5 (ppm) 20 5 20 20 2 Nd.sub.2O.sub.3 0.2 As.sub.2O.sub.3 0.5 0.5 Li + 0.741Mg + 0.367Zn 4.2 4.2 4.2 4.2 4.2 Melting temperature 1680 1680 1680 1680 1680 ( C.) Color tone b* 8.2 4.5 4.0 3.5 2.2 Transmittance (%) 87.3 88.9 86.2 89.6 90.3 Coefficient of thermal 0.9 0.9 0.9 1.0 1.0 expansion (10.sup.7/ C.)

(37) Table 1 shows Examples of the present invention (Sample Nos. 1 to 6) and Table 2 shows Comparative Examples (Sample Nos. 7 to 9). Incidentally, Sample Nos. 10 and 11 are Reference Examples.

(38) First, respective raw materials were compounded each in a form of an oxide, a hydroxide, a carbonate salt, a nitrate salt, or the like and homogeneously blended. Here, with regard to the raw materials of Al.sub.2O.sub.3, MgO, ZrO.sub.2, and SiO.sub.2, V.sub.2O.sub.5 amounts of various raw materials were previously confirmed by chemical analysis on ICP-AES and there were used raw materials in which the V.sub.2O.sub.5 amount was confirmed to be detection limit or less (detection limit: 0.07 ppm). Furthermore, the adjustment of the V.sub.2O.sub.5 amount was conducted by adding a predetermined amount of vanadium pentoxide (V.sub.2O.sub.5). In addition, as the formulation equipment and conveying equipment of the raw material batch, there were used equipments in which any V.sub.2O.sub.5-containing glass was not handled in the past.

(39) Subsequently, the resulting raw material batch was charged into a refractory furnace fitted with an oxygen combustion burner and was melted at a melting efficiency of 2.5 m.sup.2/(t/day) at a maximum temperature in the table. After the glass melt was stirred with a platinum stirrer, the melt was roll-formed in a thickness of 4 mm and further cooled to room temperature within an annealing furnace, thereby obtaining a crystallizable glass.

(40) After the crystallizable glass was subjected to a heat treatment at 760 to 780 C. for 3 hours to perform nucleation, the glass was further subjected to a heat treatment at 870 to 890 C. for 1 hour to achieve crystallization, thereby obtaining a transparent crystallized glass. For the obtained crystallized glass, the V.sub.2O.sub.5 amount, color tone, transmittance, and coefficient of thermal expansion were measured.

(41) The V.sub.2O.sub.5 amount was confirmed by chemical analysis using ICP-AES.

(42) The color tone of a transmitted light was evaluated by measuring transmittance in a wavelength range of from 380 to 780 nm using a spectrophotometer and calculating an L*a*b* value of CIE Standard from the transmittance.

(43) The transmittance was evaluated by transmittance at a wavelength of 525 nm measured using a spectrophotometer, for a crystallized glass plate, both sides of which was subjected to optical polishing into a thickness of 1.1 mm.

(44) The coefficient of thermal expansion was evaluated by an average linear coefficient of thermal expansion measured in a temperature region of from 30 to 380 C. using a glass sample processed into a solid bar of 20 mm5 mm.

(45) As is apparent from Table 1, it is revealed that the crystallized glasses of Examples all have a b* value of as small as 4.5 or less and a transmittance of as high as 89% or more.

(46) While the present invention has been described in detail and with reference to specific embodiments thereof, it will be apparent to one skilled in the art that various changes and modifications can be made therein without departing from the spirit and scope of the present invention.

(47) The present application is based on a Japanese patent application filed on May 31, 2012 (Japanese Patent Application No. 2012-124081), the contents of which are incorporated herein by reference.

INDUSTRIAL APPLICABILITY

(48) The Li.sub.2OAl.sub.2O.sub.3SiO.sub.2 based crystallized glass of the present invention is suitable for front windows of oil stoves, wood stoves, and the like, substrates for high-technology products such as color filter substrates and image sensor substrates, setters for firing electronic components, trays for microwave ovens, top plates for electromagnetic cooking, window glasses for fire-retarding doors, and the like.