TW201223907A - Optical glass, preform material, and optical element - Google Patents

Abstract

Provided are: an optical glass with which it is possible to inexpensively obtain a preform material having a high devitrification resistance and which has a refractive index (nd) and an Abbe number ( d) within a predetermined range; a preform material; and an optical element. An optical glass containing 10.0 to 50.0 mol % of a B2O3 component and 5.0 to 30.0 mol % of a La2O3 component relative to the total amount of the glass composition in terms of oxides, wherein the sum of (TiO2+WO3+Nb2O5) is 0.1 to 30.0 mol % relative to the total amount of the glass composition in terms of oxides.

Description

201223907 VI. Description of the Invention: [Technical Field of the Invention] The present invention relates to an optical glass, a preform, and an optical element. [Prior Art] In recent years, the digitalization or high definition of the machine using the light (four) system is rapidly developing, such as a digital camera or a camera, or a video playback device such as a projector or a projection television. In the field of optical equipment, the industry is strongly demanding to reduce the number of optical elements such as lenses or cymbals used in optical systems, and to reduce the weight and size of optical systems as a whole. In the optical glass for producing an optical element, in particular, it is possible to reduce the refractive index (nd) of 丨·75 or more and to have an Abbe number (Vd) of 30 or more and 50 or less in order to reduce the weight and size of the optical system as a whole. The precision-molded high-refractive-index, low-dispersion glass products are very expensive. As such a high refractive index low dispersion glass, a glass composition represented by Patent Documents 1 to 2 is known. [Prior Art Document] [Patent Document 1] Japanese Laid-Open Patent Publication No. 2001-348244 [Patent Document 2] Japanese Patent Laid-Open Publication No. 2008-001551 (Summary of the Invention) [Problems to be Solved by the Invention] The lenses used in the optical system include a spherical lens and an aspherical lens. When an aspherical lens is used, the number of optical elements can be reduced. Further, among various optical elements other than the lens, those having a complicated shape are also known. However, if a previous grinding or grinding step is to be used to obtain a non-spherical surface or form a complex shaped surface, it is costly and requires complicated operational steps. Therefore, a method of obtaining a shape of an optical element by direct press molding of a preform obtained by a glass paste ball or a glass brick by a super-precision-processed mold, that is, a method of precision press molding is currently in the mainstream. Further, in addition to the method of precision molding the preform, a glass molded body obtained by reheating and molding (reheating and press forming) a glass paste ball or a glass brick formed of a glass material is also known. Grinding and grinding methods. As a method for producing a preform for use in such precision press molding or reheat press molding, there is a method of directly producing from molten glass by a dropping method, or a method of reheating or grinding a glass brick into a spherical shape. The obtained processed product is subjected to grinding and grinding. Either way, in order to obtain the optical element in order to shape the molten glass into a desired shape, it is required to reduce the devitrification of the formed glass. Further, in order to reduce the material cost of the optical glass, it is expected that the raw material cost of each component constituting the optical glass is as inexpensive as possible. Further, in order to reduce the manufacturing cost of the optical glass, the industry expects that the melting property of the raw material is high, that is, it is melted at a lower temperature. However, the glass compositions described in Patent Documents 1 to 2 are not sufficiently suitable for these various requirements. The present invention has been made in view of the above problems, and an object thereof is to obtain a refractive index (nd) and Abbe at a lower cost. A preform having a number (vd) within a desired range and having high resistance to devitrification. [Technical means for solving the problem] The inventors of the present invention have tried to solve the above problems in a reversal of the test 159312.doc -4 - 201223907, and found that the glass containing the B2〇3 component and the La2〇3 component was found. The present invention can be completed by obtaining at least one of the Ti 2 component, the WO 3 component and the Nb 205 component as an essential component, and obtaining a desired optical constant even if the TaA 5 component which is expensive and has poor solubility is obtained. Specifically, the present invention provides the following. (1) An optical glass containing a B2〇3 component of 10.0 to 50.0% and a La2〇3 component of 5.0 to 30.0°/〇 in terms of mol% with respect to an oxide-converted composition, and Moh and ( Ti〇2+W03+Nb2〇5) The total mass of the glass relative to the oxide-converted composition is 0.1 to 30.0%. (2) The optical glass according to the above (1), wherein the content of the WO3 component is not more than 2% by mole based on the total mass of the glass of the oxide-converted composition. (3) The optical glass according to (1) above, wherein the content of the W 〇 3 component is less than 7 % by mol based on the total mass of the glass of the oxide conversion composition. (4) The optical glass according to any one of the above (1) to (3), which further comprises the following components in terms of mol% with respect to the total mass of the glass in the composition of the oxide:

Ti〇2 component 0~20.0% and/or Nb205 component 〇~2〇.〇〇/0. (7) The total mass of the glass of the optical glass of #4 (4) and (10)2.2〇5) with respect to the oxide-converted composition is 2% or more and 3% or less, as in any of the above (1) i (5). The optical glass is filled in which the molar ratio of the molar composition is W〇3/(Ti〇2+Nb2〇5+W〇3) 4 〇6〇〇 or less. (7) The optical glass according to any one of (1) to (6), wherein the total mass of the glass is 20.0% or less with respect to the oxide 1593 丨 2.doc 201223907. The content of the Li2 bismuth component is, in terms of mole %, the optical glass of the above (7), wherein the content of the u2 〇 component is expressed by G in terms of mol% with respect to the total mass of the glass in terms of oxide (9) as described above (1) The optical glass to the 'any' item, which is in terms of the total mass of the glass in terms of oxide conversion, and further contains the following

Gd203 component 〇~30.0% and/or Y2O3 component 0~10.0% and/or Yb203 component 〇~10.0% and/or Lu203 component 〇~1〇.〇〇/0. (10) The optical glass according to any one of (1) to (9) above, wherein the component (wherein Ln is one or more selected from the group consisting of La, Gd, γ, Yb, and Lu) The total mass of the ear and the composition of the oxide in terms of oxide is 10.0% or more and 40.0% or less. (11) The optical glass according to any one of the above (1) to (10), which contains two or more of the above-mentioned Ln2〇3 components. (12) The optical glass according to any one of the above (1) to (11), wherein the content of the Ta2〇5 component is 20.0°/% by mol% with respect to the total mass of the glass of the oxide conversion composition. the following. (13) The optical glass according to the above (12), wherein the molar ratio of the oxide-converted composition Ta205/W03 is 1·〇 or more and 10.0 or less. (14) The optical glass according to any one of the above (1) to (13), wherein the content of the SiO 2 component is 莫 〇 /0 159312.doc -6 - 201223907 with respect to the total mass of the glass in terms of oxide conversion composition It is 25.0% or less. (15) The optical glass of the above (14) wherein the content of the Si 〇 2 component is Η 〇 % or less based on the total mass of the glass in terms of oxide conversion. U6) The optical glass according to any one of the above (1) to (10), which further comprises the following components in terms of mol% with respect to the total mass of the glass of the oxide conversion composition:

Na20 component 0~15.0% and/or K20 component 0~1〇.〇%. (17) The optical glass according to the above (16), wherein the composition of the composition (in the formula, one or more selected from the group consisting of Li, Na, and K) and the total mass of the glass of the phase 11 in terms of oxide conversion It is 2〇〇% or less. (18) The optical glass of any one of the above (1) to (17), which has a total mass of glass relative to the oxide conversion composition, and further contains, as a component,

MgO composition 〇~10.0% and/or CaO composition 〇~ίο』% and/or SrO composition 〇~10.0% and/or BaO composition 〇~loo%. (19) The optical glass according to (18) above, wherein the R 〇 component (wherein r is one or more selected from the group consisting of Mg, Ca, Sr, and Ba) is composed of methane in terms of oxides. The total mass of the glass is below 11%. (20) The optical glass according to any one of the above (1) to (19), which has a total mass of glass in terms of an oxide conversion composition, and further contains the following 159312.doc 201223907 components in terms of mol%:

Ge02 component 0-10.0% and/or P2〇5 component 〇10.0% and/or Zr02 component 〇15.0% and/or ZnO component 〇~50.0% and/or Bi2〇3 component 〇15.0°/. And/or Te02 component 〇15.0% and/or Al2〇3 component 〇15.0% and/or Ga203 component 0~15.0% and/or Sb2〇3 component 0~1.0%, and one of the above metal elements or The fluoride partially or completely substituted by one or more of the two or more oxides is in an amount of 〇6 to 6 〇〇/〇. (21) The optical glass according to any one of the above (1) to (20) which has a refractive index (nd) of 1.75 or more and 1.95 or less and an Abbe number (vd) of 3 Å or more and 5 Å or less. (22) The optical glass according to any one of (1) to (21) above which has a glass transition point (Tg) of 68 or less. (23) Any one of the above (1) to (22) The optical glass has a liquidus temperature of 1250 ° C or lower. (24) A preform comprising the optical glass according to any one of the above (1) to (23). (25) An optical element It is produced by press-molding the preform according to the above (24). (26) An optical element which is 159312.doc 201223907 optical according to any one of the above (1) to (23) (27) An optical device comprising the optical element according to (25) or (26) above. [Effects of the Invention] According to the present invention, by using a component containing b2〇3 and ["仏The glass of the component contains one or more selected from the group consisting of a Ti〇2 component, a w〇3 component, and a Nb2〇5 component, and a desired optical constant can be obtained from a cheaper component. Therefore, it is possible to obtain a refractive index at low cost. An optical glass of a preform having a ratio (nd) and an Abbe number (Vd) within a desired range and having high resistance to devitrification. MODES OF THE INVENTION The optical glass system of the present invention contains ruthenium in the total mass of the glass in terms of oxide conversion composition; the composition is 1〇〇5〇〇% and the 1^2〇3 component is 5.0~30.0%. The total mass of the glass of the molar composition of Mo, and (Ti〇2+w〇3+Nb2〇5) relative to the oxide is 〇.1 to 30.0%. By containing a component selected from the group consisting of Ti〇2, WO3 and Nb2〇 One or more of the components consisting of 5 components, and even if the Ta2〇5 component which is expensive and less fusible is reduced, a desired optical constant can be obtained. At the same time, 'by b2〇3 component and La2〇3 component The base material has a refractive index (nd) of 1.75 or more and 1.95 or less and an Abbe number (Vd) of 30 or more and 50 or less, and the liquidus temperature tends to be low. Therefore, the refractive index (nd) can be obtained at low cost. And an optical glass of a preform having an Abbe number (Vd) within a desired range and having high devitrification resistance. The optical glass of the present invention contains an element selected from the group consisting of Ti〇2, w〇3, and Nb»2〇. One or more of the group consisting of 5 components is an essential component. It will contain 159312.doc 201223907. The glass of at least the Ti 2 component and/or the Nb 2 5 component of the WO3 component and the Nb2〇5 component will be described as the first optical glass. Further, the Ti〇2 component, the w〇3 component, and the Nb>2〇5 are contained. The glass of at least the WO3 component of the component is described as the second optical glass. Further, the optical glass of the present invention may contain both a Ti 2 component and/or a Nb 2 5 component and a w 3 component. The embodiment of the optical glass will be described in detail. The present invention is not limited to the following embodiments, and can be appropriately modified and implemented within the scope of the object of the present invention. Incidentally, the description of the overlapping description will be omitted as appropriate, but the gist of the invention is not limited. [Glass component] The composition range of each component constituting the optical glass of the present invention will be described below. In the present specification, the content of each component is expressed by mol% of the total mass of the glass in terms of oxide composition, unless otherwise specified. Here, the term "oxide-converting composition" means that when an oxide, a composite salt, or a metal fluoride which is used as a raw material of the glass constituent component of the present invention is equal to being completely decomposed and converted into an oxide at the time of melting, the formation is performed. The total mass of the oxide is set to 100 mol%, and the composition of each component contained in the glass is described. <Required component, optional component> The B2〇3 component is an essential component of the glass-forming oxide in the optical glass of the present invention containing a large amount of rare earth oxide. In particular, by setting the content of the B2〇3 component to 100% or more, the devitrification resistance of the glass can be improved and the dispersion of the glass can be reduced. Therefore, the content of the B2〇3 component is preferably 1〇〇% as the lower limit, more preferably the bO% is the lower limit, and the content is preferably 2, the ratio of 1593I2.doc 201223907 to the total mass of the glass in the oxide conversion composition. 〇〇% is set to the lower limit. On the other hand, by setting the content of the ugly 2 〇 3 component to 50% or less, a larger refractive index can be easily obtained, and deterioration of chemical durability can be suppressed. Therefore, the content of the 'Ha' component is preferably 50.0% as the upper limit, more preferably 48% by weight, and most preferably 46.0, based on the total mass of the glass of the oxide conversion composition. /. The upper limit ^heart 〇3 component can be contained in the glass by using, for example, 113; 8〇3, ν~Β4〇7, ν&2Β4〇7·10Η2〇, Bp〇4 or the like as a raw material.

The LkO3 component is a component that increases the refractive index of the glass and reduces the dispersion of the glass to increase the Abbe number of the glass. In particular, by setting the yttrium content of the La2〇3 component to 5.0% or more, the refractive index of the glass can be increased. Therefore, the amount of the La203 forming knives is preferably 5.0% as the lower limit, and more preferably 8 〇% as the lower limit, and more preferably 1 〇.〇%. The lower limit. In another aspect, the content of the La2〇3 component is set to 30.0/. Hereinafter, devitrification can be reduced by increasing the stability of the glass. It is preferable that the total mass of the glass of the composition of 2 3 knives is set to 30.0% as the upper limit, more preferably 25 〇% as the upper limit, and further preferably 20.0% as the upper limit. The best is to set 18% to the upper limit. The La2〇3 forming knives can be contained in the glass using, for example, l<n〇3)3.XH2〇 (x is an arbitrary integer) as a raw material. The optical glass of the present month is preferably one or more selected from the group consisting of a TiG2 component, a W03 component, and a 2〇5 component, and is 〇ι% or more and 3〇.〇/° or less. In particular, by using the molar ratio of 0.1% or more, even if the Taws component is reduced by 159,312.doc • 11 · 201223907, the desired optical constant can be obtained, so that the optical having the desired optical characteristics can be produced more inexpensively. glass. On the other hand, when the molar amount is 30.0% or less, the increase in the liquidus temperature due to the excessive inclusion of the components can be suppressed, so that the optical glass can be produced more stably. Therefore, it is preferable that the molar amount of the components and the glass total composition of the oxide-converted composition are 0.1% as the ητ limit, more preferably 1%% as the lower limit, and most preferably 1.5. /. Set to the lower limit. On the other hand, the molar mass of the components and the total mass of the glass relative to the oxide-converted composition are preferably set to 3 〇.〇%, more preferably 28. 〇% as the upper limit, and further preferably To set % 〇% to the upper limit, it is best to set it to less than 11〇%. In particular, in the second optical glass, from the viewpoint of further increasing the refractive index and the resistance to devitrification, it is preferable that the molar ratio of the components is 20.0% as the upper limit, and more preferably 18.0%. It is preferable that the upper limit is further set to 15.0%. The WO3 component is a component which increases the refractive index of the glass and increases the resistance to devitrification of the glass. On the other hand, by setting the content of the w〇3 component to 2 〇% or less, it is possible to form a glass which suppresses high dispersion and which has both high refractive index and resistance to devitrification. Further, by setting the content of the w〇3 component to 2% by weight or less, it is difficult to reduce the transmittance in the visible light-short wavelength region (less than 500 nm). Therefore, the content of the w〇3 component is preferably 20.0% as the upper limit, more preferably 15.0% as the upper limit, and more preferably 1% by weight, based on the total mass of the glass of the oxide-converted composition. The upper limit is best set to less than 7.0%. In particular, in the first optical glass, it is preferable that the content of the w〇3 component is 4.0% as the upper limit, and more preferably 3%%, from the viewpoint of the component which is difficult to increase the refractive index of the glass. For the upper limit, the best is set to 159312.doc •12- 201223907 is less than 1. 〇%. Further, although the optical glass of the present invention can obtain a glass having a desired optical constant and devitrification resistance even if it does not contain the w〇3 component, a higher refractive index can be obtained by containing the W〇3 component. And can further reduce the glass transfer point. Therefore, in particular, the content of the component in the second optical glass is preferably 0.1% as the lower limit, more preferably 05%, and more preferably 1.0. % is set as the lower limit, and it is preferable to set 15% as the lower limit. The w3 component can be contained in the glass using, for example, WO3 as a raw material.

The Ti〇2 component is an optional component of the optical glass of the present invention in which the refractive index and the Abbe number of the glass are adjusted to be high and the resistance to devitrification is improved. On the other hand, if the amount of TiQ2 is too large, the devitrification resistance will be deteriorated, and the transmittance of the glass under the short wavelength of visible light (below 500 nm) is also deteriorated. Therefore, the content of the component is preferably 20.0% as the upper limit with respect to the total mass 4 of the oxide-converted composition, and more preferably 15 ()% is the upper limit and 12.0% is the upper limit. Furthermore, even if the Ti〇2 component is not contained, the glass having the desired characteristics can be obtained. However, by containing the Ti〇2 component, a higher refractive index q can be obtained without lowering the glass transition property, and the refractive index can be lowered. The liquid phase temperature of the glass improves the stability... 匕, especially in the i-th optical glass, the content of the 'Ti〇2 component relative to the total mass of the glass of the oxide conversion composition' may preferably be 0.1% as the lower limit. More preferably, 3〇% is set as the lower limit, and it is preferable to set 50% to the lower limit, and it is preferable to set it to more than 8.0%.

The Ti 2 component can be contained in the glass using, for example, Ti 2 as a raw material. The component of 〇5 is an ingredient which adjusts the refractive index & dispersion of glass to a higher component as the optional component in the optical glass of the present invention. Especially by putting 159312.doc •13· 201223907

When the content of the NhO5 component is 2% or less, the deterioration of the devitrification resistance of the glass due to the excessive NhO5 component can be suppressed, and the decrease in the transmittance of the glass to visible light can be suppressed. Therefore, the content of the Nth component is preferably 2 〇〇〇 / 〇 as the upper limit, more preferably 15 〇 % as the upper limit, and more preferably 1 相对. 〇/〇 is set as the upper limit, and it is best to set 7.〇% as the upper limit. Further, although the glass having the desired characteristics can be obtained even without the NhO5 component, by containing the Nb2〇5 component, a higher refractive index can be obtained without lowering the stability of the glass, and the glass can be lowered. The liquidus temperature increases stability. Therefore, in particular, the content of the Nb:2〇5 component in the first optical glass may be preferably 下限1% as the lower limit, more preferably more than 2.0%, based on the total mass of the glass in terms of oxide conversion composition. Further, it is preferable to set 5 〇% as the lower limit, and it is preferable to set it to more than 8.0 〇/〇. The Nb2〇5 component can be contained in the glass using, for example, Nb2〇5 as a raw material. In the first optical glass of the present invention, the sum of the contents of the Ti 2 component and the 1 ^ 1 2 2 component is preferably 2.0% or more and 30.0% or less. In particular, by setting the sum to 2.0% or more, the liquid phase temperature of the glass can be lowered, and a higher refractive index can be obtained. Therefore, it is preferable that the oxide-converted composition of the first optical glass and (Ti〇2+Nb2〇5) have a lower limit of 2.0%, more preferably a lower limit of 5〇%, and further preferably Set 8.0% to the lower limit. On the other hand, by setting the sum to 30.0% or less, it is possible to suppress the deterioration of the devitrification resistance of the glass caused by the excessive content of the components. Therefore, it is preferable that the molar mass of the molar composition (Ti〇2 + Nb2〇5) relative to the oxide-converted composition is set to 3上限% as the upper limit, more preferably 25.0°/. Set to the upper limit, it is best to set 2〇〇% to the upper 159312.doc -14- 201223907 Limit 0 Again, in the first part of the present invention! Optical glass ten, WO; the ratio of the content of the component to the sum of the components of Nb2〇5 and w〇3 is preferably 0.600 or less. By narrowing the ratio, the desired Abbe number of the glass is ensured. Because of the refractive index, it is easy to obtain a glass having a desired refractive index and Abbe number. χ, because of the effect of increasing the refractive index and dispersion of the glass, Ti 2 component, Nb 2 〇 5 component And the total amount of the component of the w〇3 component is reduced. Therefore, the increase in the liquidus temperature due to the excessive inclusion of the components, that is, the devitrification, can be reduced. Therefore, the oxide in the third optical glass is converted into a molar composition. The ratio w〇3/(Ti〇2+Nb2〇5 + w〇3) is preferably an upper limit of 0.600, and more preferably an upper limit of 〇5〇〇 is set to an upper limit of 〇·37〇. On the other hand, the lower limit of the molar ratio w〇3/(Ti〇2+Nb2〇5+w〇3) in the oxide-converted composition may be 〇.

The LhO component is a component that lowers the glass transition point. In particular, by setting the content of the U2〇 component to 20.0% or less, the liquidus temperature of the glass can be lowered to reduce devitrification. Therefore, the content of the Li" component is preferably 20.0% as the upper limit, more preferably 丨5 〇% as the upper limit, and most preferably 10.0% in the glass and the enamel composition. The upper limit. Furthermore, even if it does not contain

The LhO component can also obtain a glass having desired characteristics. However, since the effect of lowering the glass transition point is increased by containing the quinone component, an optical glass which is easily press-formed can be easily obtained. Therefore, the content of the Li2 bismuth component is preferably 〇.丨% as the lower limit, more preferably 〇3°/, based on the total mass of the glass in terms of the oxide conversion composition. Set to the lower limit, the best is to set 〇 to the lower limit 0 159312.doc -15- 201223907

The GdA component is an ingredient which increases the refractive index of the glass and increases the Abbe number as an arbitrary component in the optical glass of the present invention. In particular, by setting the content of the GchO3 component to 3% by weight or less, a glass having a desired optical constant can be easily obtained, and an increase in the glass transition point (Tg) due to the excessive Gd2〇3 component can be suppressed. And can improve the resistance to devitrification of the glass. Therefore, the content of the GhO3 component is preferably set to 30.0% as the upper limit, more preferably 2%% as the upper limit, and most preferably 1%. Set to the upper limit. Further, although the Gd2〇3 component is not contained, it is technically not disadvantageous, but by replacing one of the La2〇3 components with the Gd2〇3 component, it is compared with the case where no ruthenium (12〇3 component is contained). There is a case where the temperature of the liquid phase of the glass becomes low, and there is a case where the devitrification resistance can be further improved. Therefore, the content of the Gd2〇3 component is preferably set to be larger than the total mass of the glass of the oxide conversion composition. More preferably, 〇% is 2.0%, and further preferably more than 5%. The Gd2〇3 component can be contained in the glass using, for example, Gd2〇3, GdF3 or the like as a raw material. Y2〇3 component The Yb2〇3 component and the LhO3 component are components for increasing the refractive index of the glass and reducing the dispersion, and are any component of the optical glass of the present invention, in particular, by using a Y2〇3 component, a Yb2〇3 component, and/or a Lu2 component. When the content of the 〇3 component is set to 10.0% or less, the desired optical constant of the glass can be easily obtained, and the devitrification resistance of the glass can be improved. Therefore, the components of Y2〇3, Yb2〇3, and Lu2〇3 are obtained. The content of the glass relative to the total mass of the oxide composition It is preferable to set 10.0% as the upper limit, more preferably 8 〇% as the upper limit, and most preferably 5.0% as the upper limit, especially in terms of obtaining a glass having a low glass transition point (Tg). The content of Υ2〇3 may be 159312.doc -16 - 201223907 1.3% or less. The components of Υ203, Yb203, and Lu2〇3 may be contained as raw materials using, for example, Y2〇3, YF3, Yb203, Lu2〇3, or the like. In the glass, the optical glass of the present invention is preferably a component of Lri 2 〇 3 (wherein, ^^ is one or more selected from the group consisting of La, Gd, Y, Yb, and Lu) and is 10.0%. In the above, 40_0% or less, in particular, by setting the molar ratio of the Ln2〇3 component to 10.0°/〇 or more, the refractive index of the glass and the Abbe number can be improved, so that it is easy to obtain The refractive index of the desired refractive index and the Abbe number. Therefore, the molar mass of the Ln2〇3 component and the total mass of the glass relative to the oxide conversion composition are preferably set to 10.0% as the lower limit, more preferably 12% to 5%. For the lower limit, it is preferable to set 15.0% as the lower limit. On the other hand, by setting the molar ratio of the Ln2〇3 component to 40.0% or less. Since the temperature of the liquid phase of the glass is lowered, the devitrification of the glass can be lowered. Therefore, it is preferable that the molar mass of the Ln2〇3 component and the total mass of the glass in terms of oxide conversion are 40.0% as the upper limit. 35.0°/. is set as the upper limit, and it is preferable to set the go o% as the upper limit, and it is preferable to set the upper limit to 27.0%. The optical glass of the present invention preferably contains two of the above-mentioned Ln2〇3 components. The above components, whereby the liquid phase temperature of the glass is further lowered, so that a glass having higher devitrification resistance can be formed. In particular, it is preferable to contain two or more components including a La2〇3 component and a Gd2〇3 component as the £η2〇3 component in terms of easily lowering the liquidus temperature of the glass.

The TaW5 component is a component which increases the refractive index of the glass and improves the resistance to devitrification of the glass, and is an optional component in the optical glass of the present invention. In particular, the content of the Ta2〇5 component is set to 2〇.〇〇/. Hereinafter, the devitrification caused by the excessive Ta:5〇5 component can be reduced. In addition, by reducing the amount of 159312.doc •17·201223907 in the Ta2〇5 component, the content of the expensive Ta2〇5 component can be reduced, and the temperature of the dissolved raw material can be lowered, thereby reducing the cost of the optical glass raw material and manufacturing. The cost. Therefore, it is preferable to set the content of the Ta2〇5 component to the total mass of the glass of the oxide-converted composition to 20.0% as the upper limit, and more preferably to set the upper limit of 1% to the upper limit. . In particular, the content of the 'Ta2〇5 component in the first optical glass may be 4.5% or less. Further, even if the Τα〇5 component is not contained, a glass having desired characteristics can be obtained, but in particular, in the second optical glass, the refractive index of the glass can be increased by including the τ & 2 〇 5 component. Further, it is possible to increase the resistance to devitrification by lowering the liquidus temperature of the glass. Therefore, the content of the Ta2〇5 component in the second optical glass is preferably set to be more than 〇% based on the total mass of the glass in terms of oxide conversion composition. More preferably, 1.0% is set as the lower limit, and it is preferable to set 2%% to the lower limit. The Ta2〇5 component can be contained in the glass using, for example, Ta2〇5 as a raw material. The second optical glass of the present invention preferably has a ratio of the content of the Ta 2 〇 5 component to the amount of the W 〇 3 knives of 1 〇 or more. In particular, by setting the ratio to 1.0 or more, the visible light transmittance of the glass can be maintained, the refractive index can be increased, and the increase in dispersion of the glass can be suppressed. Further, since the temperature of the liquid phase of the glass is lowered, the devitrification resistance of the glass can be improved. Therefore, it is preferable that the molar ratio Ta205/W03 of the oxide-converted composition in the second optical glass is 丨0 as the lower limit, more preferably 2_0 as the lower limit, and further preferably 21 as the lower limit. To set 2.5 to the lower limit. On the other hand, the upper limit of the ratio is not particularly limited, and may be infinite (i.e., does not contain the WQ3 component). However, by setting the ratio to 10.0 or less, the amount of the expensive component can be reduced, so that the cost of the optical glass and the cost of manufacturing can be reduced. 159312.doc 201223907 The Moir ratio Ta2〇5/w〇3 of the oxide conversion composition in the 'second optical glass is preferably 1 〇·〇 as the upper limit, and more preferably 7 〇 as the upper limit. The best is to set 4.0 as the upper limit.

The SiCh component is a component which is a component of the optical glass of the present invention which improves the viscosity of the molten glass and lowers the component of the optical glass which is less devitrified (the production of crystals) by promoting the formation of a stable glass. In particular, the content of the Si〇2 component was set to 25.0 Å/. In the following, the rise of the glass transition point (Tg) can be suppressed, and the high refractive index which is the object of the present invention can be easily obtained. Therefore, the content of the Si 2 component is preferably 25.0 with respect to the total glass mass of the oxide-converted composition. /. The upper limit is set, and it is more preferable to set 19% to the upper limit', and it is preferable to set the upper limit of 17.5%, and it is preferable to set 13% to the upper limit. Further, even if the Si 〇 2 component is not contained, a glass having desired characteristics can be obtained, but in particular, in the second optical glass, the liquid phase temperature of the glass is lowered by containing the S 〇 2 component. Therefore, the devitrification of the glass can be reduced. Further, by increasing the viscosity of the molten glass, the glass can be easily formed. Therefore, the content of the 'Si 2 component is preferably more than 0% with respect to the total mass of the oxide-converted composition. It is more preferably set to more than 1.%, and most preferably set to more than 4.0. /〇. The Si 2 component can be contained in the glass using, for example, SiO 2 , K 2 SiF 6 , NazSiF 6 or the like as a raw material.

The NaaO component and the κ:2〇 component are components which improve the meltability of the glass, lower the glass transition point, and improve the devitrification resistance of the glass, and are arbitrary components in the optical glass of the present invention. In particular, by setting the content of the Na20 component to 15% or less and/or setting the content of the κζ〇 component to be less than or equal to or less, the refractive index of the glass is hard to be lowered, and the stability of the glass can be improved. Reduced 159312.doc -19- 201223907 Devitrification and so on. Therefore, the content of the Na2 bismuth component is preferably 15.0% as the upper limit, more preferably 1 〇·〇% as the upper limit, and most preferably 5.0 °/%. Set to the upper limit. Further, it is preferable that the content of the Κ2 〇 component is 10.0% as the upper limit, and more preferably 8 〇% as the upper limit, and more preferably 5 as the upper limit. For the NaW component and the ho component, for example, Na2c〇3 can be used.

NaN03, NaF, Na2SiF6, K2C03, KN03, KF, ΚΗΙ2, and K2SiF6 are contained in the glass as a raw material.

The RhO component (wherein Rn is one or more selected from the group consisting of ruthenium and osmium) is a component which improves the meltability of the glass and lowers the devitrification of the glass. Here, by setting the content of the 11112〇 component to 2 〇% or less, it is difficult to lower the refractive index of the glass, and the stability of the glass can be improved to reduce the occurrence of devitrification or the like. Therefore, it is preferable that the molar mass of the RhO component and the total mass of the glass in terms of the oxide conversion composition be 2%% as the upper limit, more preferably 15.0% as the upper limit, and most preferably 1%%. The upper limit.

The MgO component, the Ca0 component, the Sr〇 component, and the Ba〇 component are components which adjust the refractive index, meltability, and devitrification property of the glass, and are arbitrary components in the optical glass of the present invention. In particular, by setting the content of each of the Mg bismuth component, the Ca 〇 component, the Sr 〇 component, and the Ba 〇 component to 1% by mole or less, the desired refractive index can be easily obtained, and the excessive inclusion of the components can be reduced. The resulting glass is devitrified. Therefore, it is preferable that the content of each of the Mg 〇 component, the Ca 〇 component, the 〇 component, and the Ba Ο component is in the total amount of the glass in terms of the oxide conversion composition, and it is preferable to set the upper limit to be 10.0%, and more preferably to set the upper limit to 80%. For the upper limit, it is best to set 5.0% as the upper limit. For the Mg0 component, for example, MgC〇3, 159312.doc •20·201223907 can be used.

MgF2, CaC〇3, CaF2, core (10) 3)2, SrF2, BaC〇3' Ba(N〇3) 2, and secret 2 are contained in the glass as a raw material. The optical glass of the present invention preferably has a total content of the R 〇 component (wherein Μ is selected from one or more of the group consisting of Mg, Ca, Sr, and Ba) is 11.0 /. the following. Thereby, the desired refractive index can be easily obtained. Therefore, it is preferable to set 11.0% as the upper limit, and more preferably 8 〇% as the upper limit, and it is preferable to set 5.0% as the upper limit of the composition of the RO to I and the total mass of the glass. Upper limit.

The Ge〇2 forming tool is a component having an effect of increasing the refractive index of the glass and improving the resistance to devitrification, and is an arbitrary component in the optical glass of the present invention. However, since Ge02 has a relatively high raw material price, if the amount thereof is large, , the production cost becomes higher, and thus the effect produced by lowering the TkO5 component is impaired. Therefore, it is preferable to set 10.0% as the upper limit, and more preferably 50% as the upper limit, and preferably 1 to 〇/〇- The upper limit. The Ge 2 component can be contained in the glass, for example, by using it as a raw material. The P2〇5 component is a component having an effect of lowering the liquidus temperature of the glass and improving the devitrification resistance, and is an optional component in the optical glass of the present invention. In particular, by setting the content of the P2〇5 component to 1% by weight or less, the chemical durability of the glass, particularly the water resistance, can be suppressed. Therefore, it is preferable to set the content of the P2〇5 component to the total mass of the glass in terms of the oxide conversion composition, preferably to set the upper limit to 100%, and more preferably to set the upper limit to 80%, preferably to 50%. The upper limit. For the P205 component, for example, A1(P〇3)3, Ca(p〇3)2'Ba(p〇3)2, BPO4, and H3P〇4 can be used as a raw material and contained in the glass. 159312.doc •21- 201223907

The Zr〇2 component is a component which contributes to the high refractive index and low dispersion of the glass and improves the devitrification property of the glass. However, if the amount of Zr〇2 is too large, the resistance to devitrification deteriorates by β. Therefore, the content of the Zr〇2 component is preferably 15.0 °/% based on the total mass of the glass in terms of oxide conversion. It is preferable to set the upper limit to 12 〇%, and it is preferable to set the upper limit to 10.0%. Further, although the bismuth 2 component is not contained, a glass having desired characteristics can be obtained, but By containing the Zr〇2 component, the high refractive index and low dispersion property can be easily obtained, and the effect of improving the devitrification property can be easily obtained. Therefore, in particular, in the second optical glass, the content of the Zr〇2 component is preferably set to more than 0% by mass based on the total mass of the glass in terms of oxide composition, and more preferably 1.0%. Set to the lower limit, and it is best to set 3.0% as the lower limit. The ZrO 2 component can be contained in the glass using, for example, ZrO 2 , ZrF 4 or the like as a raw material.

The ZnO component is a component which lowers the glass transition temperature (Tg) and improves chemical durability, and is an optional component in the optical glass of the present invention. However, if a large amount of the ZnO component is contained, the devitrification resistance of the glass is likely to deteriorate. Therefore, the content of the ZnO component is preferably 50.0% as the upper limit, more preferably 45.0 °/, based on the total mass of the glass in terms of oxide conversion. The upper limit is set, and it is more preferable to set 40.0% as the upper limit. In particular, the content of the ZnO component can be 27.0% or less with respect to the total mass of the oxide-converted composition, and can be set to less than 24.0%, from the viewpoint of improving the stability of the glass and lowering the liquidus temperature. Further, although a glass having desired characteristics can be obtained without containing a ZnO component, the glass transition point is lowered by containing a ZnO component, so that an optical glass 159312.doc which is more easily formed by pressure can be easily obtained. •22·201223907 Glass° Therefore, it is preferable that the content of the ZnO component is more than 〇% with respect to the total composition of the oxide-converted composition, and it is more preferable to set 5 〇% as the lower limit, and it is preferable to set 10.0%. Lower limit. The Zn0 component can be contained in the glass using, for example, Zn〇, ZnF2 or the like as a raw material.

The Bi2〇3 component is a component which increases the refractive index and lowers the glass transition point (Tg) and is an arbitrary component in the optical glass of the present invention. Especially by

When the content of the BiZ〇3 component is set to 15.5% or less, the liquidus temperature can be suppressed from rising, so that the deterioration of the devitrification resistance of the glass can be suppressed. Therefore, the amount of the Bi2〇3 knives is preferably set to 15.0% as the upper limit of the total amount of the glass of the oxide conversion composition, and more preferably set to less than 1% by weight, and most preferably set to less than 5·〇%. The Bi2〇3 component can be contained in the glass by using, for example, 2〇3 or the like as a raw material.

The Te〇2 component is an ingredient which increases the refractive index and lowers the glass transition point and is an optional component in the optical glass of the present invention. • However, Te02 has a problem of alloying with platinum when the glass raw material is melted in a melting tank formed of platinum (5) or a molten glass. The content of the 'Te02 component is preferably 15.0% as the upper limit, more preferably less than 1%, and most preferably less than 5%, based on the total mass S of the oxide-converted composition. 0%. The Te〇2 component can be contained in the glass using, for example, scratching or the like as a raw material.

The Al2〇3 component and the Ga2〇3 component are components which improve the chemical durability of the glass and improve the devitrification resistance of the molten glass, and are arbitrary components in the optical glass of the present invention. In particular, by setting the content of each of the 〇3 component and the 〜2〇3 component to be lower than hereinafter, it is possible to reduce the devitrification tendency of the glass by improving the stability of the glass. Therefore, the content of each of the Ah 〇 3 component and the (^ 2 〇 3 component is preferably 150% as the upper limit, and more preferably 10.0% as the upper limit, the total mass of the glass in terms of the oxide conversion composition. It is preferable to set 5 〇% as the upper limit. The Al2〇3 component and the Ga2〇3 component can be contained as raw materials using, for example, Al2〇3, a1(〇h)3, A1F3, Ga2〇3, Ga(OH)3 or the like. In the glass, the component of St 2 is a component which defoams the molten glass, and is an arbitrary component in the optical glass of the present invention. If the amount of Sb»2〇3 is too large, the transmittance in the short-wavelength region of the visible light region Therefore, the content of the Sb2〇3 component is preferably an upper limit of 1% by weight, more preferably 0.7% of the upper limit, and most preferably 〇5%, based on the total mass of the glass of the oxide conversion composition. The upper limit is sb203, Sb2〇5, Na2H2Sb207.5H20, etc., and is contained in the glass as a raw material. Further, the component for clarifying and defoaming the glass is not limited to the above sb2〇3 component. A well-known clarifying agent, antifoaming agent or a combination of these in the field of glass manufacturing is used. The dispersion of the glass, and the reduction of the glass transition point (Tg), and the component for improving the devitrification resistance, are arbitrary components in the optical glass of the present invention. However, if the content of the F component is one or both of the above metal elements, When the total amount of fluoride in some or all of the above-mentioned oxides is more than 6.0 in terms of F, the amount of volatilization of the F component increases, so that it is difficult to obtain a stable optical constant, and it is difficult to obtain a homogeneous glass. The content of the F component is preferably 6.0% as the upper limit, more preferably 5. 〇% as the upper limit, and most preferably 3 〇% as the upper limit. It can be contained in glass by using, for example, ZrF4, A1F3, NaF, CaF2, etc., 159312.doc.24·201223907 as a raw material. <About the component which should not be contained> Then, the optical glass which should not be included in the present invention The components and the components which are preferably not contained are described. Other components may be added as needed in the process of not impairing the characteristics of the glass of the invention of the present application, in addition to Ti, Zr, Nb, W, La, Gd Than Y, Yb, Lu, V, Cr, Μη, Fe, Co, Ni, Cu, Ag and

Various transition metal components such as Mo, even when they are contained alone or in a small amount, have the property of being colored by glass and absorbing at a specific wavelength in the visible light range, and therefore, especially in an optical glass using a wavelength of a visible light region, It is preferably substantially not contained. Further, since a lead compound such as PbO or an arsenic compound such as As2〇3 is a component having a high environmental load, it is preferably substantially not contained, i.e., it is not contained at all except for inevitable mixing. Further, each of Th, Cd, Tl, Os, Be, and Se has a tendency to be controlled and used as a harmful chemical substance in recent years, and it is considered that it is required not only in the glass production step but also in the processing step and the post-product processing. Measures on the countermeasures against the environment. Therefore, when it is important to pay attention to the influence of the environment, it is preferable that the content is not substantially contained.曰^ The glass composition of the present invention is represented by the % of the total mass of the glass converted in terms of oxides, and thus is not directly represented by the quality, but in the present invention, it exists to satisfy the requirements. The composition of each of the various compositions in the glass composition is expressed by mass% by (4): the following values are obtained by changing the composition: 159312.doc -25- 201223907 B2〇3 composition 5.0 to 25.0% by mass, and La203 Component: 10.0 to 55.0% by mass, W03 component 0 to 30.0% by mass, and/or TiO 2 component 0 to 10.0% by mass and/or Nb205 component 0 to 3 5.0% by mass and/or Li20 component 0 to 5.0% by mass and/or Gd203 component 0 to 5 5.0% by mass and/or Y2〇3 component 〇~20.0% by mass and/or Yb203 component 0 to 25.0% by mass and/or Lu203 component 0 to 20.0% by mass and/or Ta205 component 0 to 30.0% by mass and/or Or SiO 2 component 0 to 10.0% by mass and/or Na20 component 0 to 8.0% by mass and/or K20 component 0 to 8.0% by mass and/or MgO component 0 to 3.0% by mass and/or CaO component 0 to 5.0% by mass/〇 And/or SrO component 0 to 8.0% by mass and/or BaO component 0 to 10.0% by mass and/or Ge0 2 components 0 to 7.0% by mass and/or P2〇5 component 〇~1〇.〇% by mass and/or Zr02 component 0 to 12.0% by mass and/or ZnO component 0 to 30.0% by mass and/or Bi203 component 0 to 40.0 Mass ° / 〇 and / or Te02 composition 0-15.0% by mass and / or -26- 159312.doc 201223907

Al2〇3 composition 〇~12 〇 mass. /. And/or

The GaW3 component is 0 to 20% by mass and/or the Sb203 component is 〇3 to 3% by mass, and the fluoride which is partially or completely substituted with one or more of the above-mentioned metals &amp; The total amount is 〇~3〇% by mass. [Production Method] The optical glass of the present invention can be produced, for example, in the following manner. That is, by uniformly mixing the ingredients in a range in which the respective components are within a specific content, and putting the produced mixture into a platinum smash, the temperature range of the ～15Gn: is given according to the glaze of the glass composition. (10) After the smelting hours and homogenization of the money, the temperature is lowered to an appropriate temperature, and then the scale is washed in a mold and slowly cooled to be produced. [Physical Properties] The optical glass of the present invention has a high refractive index (nd) and a low dispersion. In particular, the refractive index (nd) of the optical glass of the present invention is preferably 175 as the lower limit, more preferably L77 as the lower limit, and most preferably 18 〇 as the lower limit, preferably 1.95 as the upper limit. More preferably, 192 is set as an upper limit, and it is preferable to set 1.91 as an upper limit. Further, the Abbe number (vd) of the optical glass of the present invention is preferably such that 30 is the lower limit, more preferably 31 is the lower limit, and most preferably 32 is the lower limit, and preferably 5 is set as the upper limit. More preferably, 45 is set as an upper limit, and it is preferable to set 40 as an upper limit, whereby the degree of freedom in optical design can be increased, and even if the element is made thinner, a large amount of light can be obtained. Further, the optical glass of the present invention preferably has less coloration. In particular, if the optical glass disclosed in Japanese Patent Publication No. 159312.doc -27-201223907 is expressed by the glass transmittance, the wavelength (λ7❶) of the light transmittance of 70% in the sample having a thickness of 1 mm 2 is 45 〇 nm. Hereinafter, it is more preferably 430 nm or less, and most preferably 42 〇 nm or less. It is also shown that the wavelength (λ5) of the 5% light transmittance is 400 nm or less, more preferably 38 〇 nmw, and most preferably 370 nm or less. Further, the wavelength (kc) of the spectral transmittance of 8〇% is 550 nm or less, more preferably 52 Å or less, further preferably 500 nm or less, and most preferably 480 nm or less. Thereby, since the absorption limit of the glass is in the vicinity of the ultraviolet ray region and the transparency of the glass in the visible light range is increased, the optical glass can be preferably used as a material of an optical element such as a lens. Further, the optical glass of the present invention preferably has high resistance to devitrification. In particular, the optical glass of the present invention preferably has a lower liquidus temperature of 120 (rc or less. More specifically, the liquidus temperature of the optical glass of the present invention is preferably 1200 ° C as an upper limit, more preferably In order to set U8〇〇c as the upper limit, it is preferable to set 1160 C as the upper limit. Therefore, even if the molten glass flows out at a lower temperature, the crystallization of the produced glass is lowered, so that the self-melting state can be formed. The resistance to devitrification in the glass raft can reduce the influence on the optical characteristics of the optical element using glass. Moreover, since the temperature range of the stable production of the preform material is widened, even if the melting temperature of the glass is lowered, it can be formed. The preform material 'suppresses the energy consumed in the formation of the preform. On the other hand, the lower limit of the liquidus temperature of the optical glass of the present invention is not particularly limited, but the liquid phase temperature of the glass obtained by the present invention is mostly In this case, it is approximately 500 ° C or more, specifically 55 (rc or more, more specifically 6 〇〇 &lt; t or more. Further, the "liquidus temperature" in the present specification is expressed at 5 〇 159312. .doc

• 28·201223907 ml of white gold crucible, put 3 cc glass-like glass sample into platinum crucible, completely melted at 1250 ° C, cool down to a specific temperature and keep After 12 hours of taking out to the outside of the furnace and cooling, the presence of crystals in the glass surface and the glass was observed immediately, and the lowest temperature of crystallization was not observed. Here, the term "specific temperature" means a temperature set at 10 ° C from 丨丨 8 〇 t &gt; c to 500 ° C. Further, the optical glass of the present invention has a glass transition point (Tg) of 680 ° C or lower. Thereby, since the glass is softened at a lower temperature, the glass can be easily press-formed at a lower temperature. Further, it is possible to reduce the oxidation of the mold used for the press forming and to increase the life of the mold. Therefore, the glass transition point (Tg) of the optical glass of the present invention preferably has an upper limit of 68 〇 t:, more preferably 650 ° C as an upper limit, and most preferably 630. Further, the lower limit of the glass transition point (Tg) of the optical glass of the present invention is not particularly limited. The glass transition point (Tg) of the glass obtained by the present invention is, in most cases, approximately 100 〇C. The above is specifically ι5 〇β (: above, more specifically 200. (: above. Further, the optical glass of the present invention preferably has a deformation point of 720 ° C or lower (At) ° deformation point (At In the same manner as the glass transition point (Tg), one of the indexes indicating the softening property of the glass is an index indicating the temperature close to the press molding temperature. Therefore, the deformation point (At) is 72 〇 ° or less. The glass can be press-formed at a lower temperature, so that press forming can be performed more easily. Therefore, the deformation point (At) of the optical glass of the present invention preferably has 72 〇〇c as an upper limit, and It is preferable to set 7 〇 (rc as the upper limit, and it is preferable to set 68 〇〇c as the upper limit. Furthermore, the lower limit of the deformation point (At) of the optical glass of the present invention is not 159312.doc •29·201223907 'The deformation point (At) of the glass obtained by the present invention is mostly large It is 150 ° C or more, specifically 200 ° C or more, more specifically 250 ° C or more. Further, the optical glass of the present invention preferably has a lower partial dispersion ratio (0 g ' F ) ° more specific In contrast, the partial dispersion ratio (eg 'f) and the Abbe number (Vd) of the optical glass of the present invention satisfy (_2 5〇xlo-3xVd+〇6571) $(98,?)$(-2.50&gt;&lt; The relationship between 1〇\, +〇.6971), whereby an optical glass having a small partial dispersion ratio (eg 'F) can be obtained, so that the chromatic aberration of the optical element formed by the optical glass can be reduced. The partial dispersion ratio (0g, F) of the optical glass is preferably such that (_2.50xl (T3xvd+0.6571) is the lower limit, and more preferably (-2.5〇xl〇-3XVd+0.6591)s is the lower limit, and the best is (•2,5〇xl(T3xvd+〇.6611) is set as the lower limit. On the other hand, the partial dispersion ratio (eg, F) of the optical glass of the present invention is preferably (_2 5〇xl〇-3XVd+ 0.697 1 It is better to set the upper limit to (_2 5〇xl〇-3XVd+〇6921) as the upper limit. The best is to set (-2.5〇xl〇-3xVd+〇.6871) to the upper limit. [Preform and optical Component] can be made using In the optical glass, a glass molded body is produced by a press molding method such as reheat press molding or precision press molding, that is, a preform for press molding can be produced by using optical glass, and the preform can be reheated and pressed. Thereafter, a glass molded body is produced by polishing, or a preform formed of the polishing process or a preform molded by a known floating molding or the like is subjected to precision press molding to produce a glass molded body. Furthermore, the means for producing the glass molded body is not limited to these means. Thus, the optical glass of the present invention can be used in various optical components and optical devices 159312.doc • 30·201223907. In particular, it is preferable to form a preform by using the optical glass of the present invention, and to perform an optical element such as a lens or a crucible by reheating or press molding or precision press molding using the preform. As a result, an optical element can be increased in size by forming a preform having a large diameter. When used in an optical device such as a camera or a projector, high-definition and high-precision imaging characteristics and projection characteristics can be realized. [Examples] The compositions of the examples (No. 1 to No. 105) and the comparative examples (No. A) of the present invention, and the refractive index (nd), Abbe number (Vd), and partial dispersion of the glasses. The results of the ratio (0g, F), glass transition point (Tg), deformation point (At), liquid phase temperature, spectral transmittance showing 5%, 70% and 80% of wavelength %, λ7 〇 and λ80) are shown in Table 1 to Table 14. Further, the examples (No. 1 to Νο_ 12) are examples of the first optical glass. The examples (Νο· 1~Νο· 2, No. 13 to No. 105) are related to the implementation of the second optical glass. example. Further, the following examples are for illustrative purposes only and are not limited to the embodiments. The glass of the shell examples (N 〇. 1 to N 〇 10 5 ) and the comparative example (No. A) of the present invention are produced by selecting respective suitable oxides, hydroxides, carbonates And a high-purity raw material used for a usual optical glass such as a nitrate, a fluoride, a hydroxide, or a metaphosphoric acid compound, as a raw material of each component, in such a manner as to be a ratio of the components of the respective examples shown in Tables 1 to 14. Weighing and evenly mixing, and then putting it into platinum, and melting it in the temperature range of 1丨(10)~丨5〇〇°c for 2 to 5 hours according to the melting difficulty of the glass composition, and then homogenizing and stirring. Then, it is cast into a mold or the like and slowly cooled. 159312.doc •31- 201223907 Here, the refractive index (nd), Abbe's number (vd) and partial dispersion ratio (0g) of the glass of 'Examples (No. 1 to No. 105) and Comparative Example (No. A) , F) is measured based on the Sakamoto Optical Glass Industry Association specification JOGIS01-2003. Further, with respect to the obtained Abbe's number (vd) and partial dispersion ratio, and the value of F), the intercept b when the slope a in the relational expression (eg ‘ F) = -axvd + b is 0.0025 is obtained. Here, the refractive index (nd), the Abbe number (vd), and the partial dispersion ratio (Qg, F) are determined by measuring the glass obtained by setting the slow cooling rate to -25 ° C /hr. Out. Further, the glass transition point (Tg) and the deformation point (At) of the glass of the examples (No. 1 to No. 105) and the comparative example (No. A) were determined by measurement using a transverse expansion type measuring device. . Here, the sample used for the measurement was used with a length of 4.8 mm and a length of 50 to 55 mm, and the temperature increase rate was set to 4. (:/min. The glass transmittance of the examples (No. 1 to No. 105) and the comparative example (No. A) was measured based on the Japanese Optical Glass Industrial Association specification J〇GiS〇2. In the present invention, the presence or absence of the color of the glass is determined by measuring the transmittance of the glass. Specifically, the face-parallel grinding product having a thickness of 10 ± 0.1 mm is measured based on JIS Z8722 200 to 800 nm. The split light transmittance 'determines λ5 (wavelength at a transmittance of 5%), λ70 (wavelength at a transmittance of 70%), and λ8〇 (wavelength at a transmittance of 80%). The liquidus temperature of the glass of the examples (No. 1 to No. 105) and the comparative example (Ν〇·Α) was in a platinum crucible of a volume of 50 ml, and a glass crumb-like glass sample of 3 cc was used. Put the platinum into the vortex and let it completely melt at 1250 °c, and cool down to 118 〇·&gt; (:~1000^ at any temperature set by (7) for 12 hours' After cooling, immediately observe I59312.doc •32· 201223907 Check the presence or absence of crystals on the glass surface and glass, and find the lowest temperature at which no crystallization is observed. [Table 1] Example 1 2 3 4 5 6 7 S B2〇3 33.680 43.931 44.931 44.931 31.773 31.268 39.996 26.222 La2〇3 15309 16.676 16.676 16.676 14.783 11.984 16.499 14.617 W03 2.987 3.473 7.785 6.941 15.498 Ti02 5.103 8.300 10.770 8.300 10.260 Nb2〇 5 2.470 9.407 8.210 10.499 4.414 Li20 2.056 2.056 2.056 0.767 0.755 3.498 Gd2〇3 10.206 5.411 5.411 5.411 2.304 2.297 Y203 0.364 Yb2〇3 Lll2〇3 Ta2〇5 3.062 3.830 3.830 3.830 Si02 10.206 4.709 4.634 11.601 Na20 K20 MgO CaO SrO BaO Ge〇 2 P2〇5 Zr02 4.082 4.956 4.956 4.956 3.615 6.992 ZnO 15.309 11.309 11.309 11.309 30.767 30.278 13.999 23.233 A1203 Sb2〇3 0.056 0.059 0.059 0.059 0.010 0.010 0.011 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ti+Nb+W 8.090 11.773 10,770 10.770 17.192 15.152 25.998 14.674 Ti+Nb 5.103 8.300 10.770 10.770 9.407 8.210 10.499 14.674 W/(Ti+Nb+W) 0.369 0.295 0.000 0.000 0.453 0.458 0.596 0.000 La+Gd+Y+Yb+Lu 25.515 22.087 22.087 22.087 14.783 14.288 16.499 17.278 Ln number 2 2 2 2 1 2 1 3 Ta/W 1.025 1.103 - - 0.000 0.000 0.000 - Li+Na+K 0.000 2.056 2.056 2.056 0.767 0.755 3.498 0.000 Mg+Ca+Sr+Ba 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 nd 1.87183 1.87664 1.8734 1.88250 1.89469 1.89234 1.90221 1.90425 vd 39.1 36.9 37.4 36.6 32.7 33.2 31 35.6 Partial dispersion ratio (eg, f) 0.57348 0.57817 0.57870 0.57919 0.59000 0.58607 0.59450 Intercept b (a=0.00250) 0.67123 0.67042 0.67220 0.67069 0,67175 0.66907 0.67200 Tg(°C) 621 At(°C) 664 λ8〇[ηηι] 441.5 464.5 447 452 452 493 489.5 λ7〇[ Ηπι] 396 406 402 402 393.5 412.5 401.5 λ5[ηηι] 351 357.5 354 353 353.5 361 353 Liquid phase temperature (°c) 1120 1060 1080 1080 1160 -33- 159312.doc 201223907 [Table 2] Example Comparative Example 9 10 11 12 13 14 15 16 A B2〇3 38.80 30.27 27.98 28.944 29.23 29.00 30.90 28.94 33.560 L32〇3 16.50 11.87 10.64 10.291 15.11 16.00 15.97 14.96 21 .330 W〇3 3.51 3.12 3.140 2.65 1.90 1.79 1.74 Ti〇2 10.19 6.03 7.33 7.337 Nb205 2.444 Li20 2.034 1.047 1.062 1.065 0.794 0.794 Gd2〇3 7.332 7.325 9.968 11.216 4.613 5.000 4.877 4.567 7.952 Y203 1.771 Yb2〇3 Lu2〇3 0.018 Τ ^2〇5 3.789 2.813 6.852 5.150 4.762 4.347 8.574 Si02 7.649 6.905 7.335 7.356 7.876 8.810 8.327 7.798 16.714 Na20 K20 MgO CaO SrO BaO Ge02 P205 Zr02 4.487 4.646 4.659 4.225 4.189 4.466 4.183 10.100 ZnO 11.188 25.701 27.894 25.966 29.388 29.900 28.066 32.625 AI2O3 Sb2〇 3 0.058 0.024 0.023 0.026 0.058 0.054 0.051 0.054 Total 99.98 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ti+Nb+W 12.634 9.537 10.445 10.478 2.650 1.900 1.786 1.738 0.000 Ti+Nb 12.634 6.031 7.326 7.337 0.000 0.000 0.000 0.000 0.000 W/(Ti+ Nb+W) 0.000 0.368 0.299 0.300 1.000 1.000 1.000 1.000 - La+Gd+Y+Yb+Lu 23.830 19.211 20.609 21.50 7 19.719 21.000 20.847 19.523 31.053 Ln number 2 3 2 2 2 2 2 2 3 Ta/W - 0.802 0.000 0.000 2.586 2.711 2.667 2.501 - Li+Na+K 2.034 1.047 1.062 1.065 0.000 0.000 0.794 0.794 0.000 Mg+Ca+Sr+ Ba 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 nd 1.87574 1.87336 1.87306 1.87822 1.86728 1.85905 1.85873 1.88737 vd 37.1 37.6 37.8 38.7 40.1 40.8 40.5 40.4 Partial dispersion ratio (eg,f) 0.57766 0.57849 0.57792 0.57212 0.56872 0.56770 0.56866 0.56655 Intercept b (a= 0.00250) 0.67041 0.67249 0.67242 0.66887 0.66897 0.66970 0.66991 0.66755 Tg(°C) AtCt) X^〇[nm] 447 429 411.5 410.5 405.5 456 λ7〇[ηπι] 393.5 382.5 375 371 369.5 378 ^5[nm] 351 342.5 338.5 336 336 321 Liquidus temperature (°c) 1260 • 34- 159312.doc 201223907 [Table 3] Example 17 18 19 20 21 22 23 24 B2〇3 32.952 32.343 31.597 32.909 32.952 32.995 30.950 33.691 L&amp;2〇3 14.052 13.639 13.657 15.323 14.052 12.777 15.037 14.363 W〇3 Ti02 8.617 9.707 8.861 8.606 8.617 8.628 4.12 7 Nb2〇5 2.772 4.266 Li20 0.985 0.963 0.964 0.984 0.985 0.987 1.155 1.104 Gd2〇3 4.058 3.740 3.745 2.894 4.058 5.225 4.342 4.153 Yi〇3 Yb203 LU2O3 Τ&amp;2〇5 4.658 4.294 4.300 4.652 4.658 4.664 4.985 3.108 Si02 6.348 5.851 5.859 6.339 6.348 6.356 6.793 6.490 6.490 Na20 K20 MgO CaO SrO BaO p2〇5 Zr02 5.155 4.752 4.758 5.148 5.155 5.162 5.516 5.038 ZnO 23.175 24.711 26.260 23.145 23.175 23.206 28.450 23.660 〇3·2〇3 Sb2〇3 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ti+ Nb+W 8.617 9.707 8.861 8.606 8.617 8.628 2.772 8.393 Ti+Nb 8.617 9.707 8.861 8,606 8.617 8.628 2.772 8,393 W/(Ti+Nb+W) 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 La+G d+Y+Yb+Lu 18.110 17.380 17.402 18.217 18.110 18.003 19.379 18.516 Ln number 2 2 2 2 2 2 2 2 Ta/W - - - - - - - - Li+Na+K 0.985 0.963 0.964 0.984 0.985 0.987 1.155 1.104 Mg+Ca+Sr+Ba 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 nd 1.87882 1.88154 1.88028 1.87995 1.88067 1.87797 1.87268 1.88245 vd 36.7 36.1 36.4 36.7 36.7 36.7 39.0 36.4 Partial dispersion ratio (9g, F) 0.57822 0.5S078 0.57899 0.57923 0.57875 0.57871 0.57098 0.57927 Intercept b (a=0.00250) 0.66997 0.67103 0.66999 0.67098 0.67050 0.67046 0.66848 0.67027 Tgfc) 616 AtfC) 655 λ8〇[ηιτι] 464.5 472 479.5 477.5 490.5 452.5 475.5 432 λ7〇[ηιη] 384 389 387 384.5 384 385.5 376.5 381 λ5[ηηι] 348 349.5 348 347.5 347 348.5 317.5 342.5 Phase temperature (°c) 1,100 1,100 1,100 1,110 1,120 1,120 1,160 1,140 35- 159312.doc 201223907 [Table 4] Example 25 26 27 28 29 30 31 32 B203 33.723 33.768 33.814 33.723 33.768 33.814 33.973 32.426 La2〇3 17.680 16.381 15.078 17.680 16.381 15.078 14.199 15.730 W03 1.334 Ti02 4.131 4.137 4.142 4.131 4.137 4.142 5.699 Nb2〇5 3.191 3.195 3.199 3.191 3.195 3.199 4.465 2.549 Li20 1.105 1.106 1.108 1.105 1.106 1.108 1.113 1.062 Gd2〇3 1.188 2.378 3.572 1.188 2.378 3.57 2 2.393 2.284 y2〇3 Yb203 LU2O3 Ta205 3.761 3.766 3.771 3.761 3.766 3.771 4.116 2.991 Si02 6.496 6.505 6.514 6.496 6.505 6.514 4.138 6.247 Na20 K20 MgO CaO SrO BaO P2O5 Zr02 5.043 5.050 5.056 5.043 5.050 5,056 5.080 4.849 ZnO 23.683 23.714 23.746 23.683 23.714 23.746 29.188 26.163 G&amp;2〇3 Sb2〇3 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ti+Nb+W 7.322 7.332 7.341 7.322 7.332 7.341 5.800 8.248 Ti+Nb 7.322 7.332 7.341 7.322 7.332 7.341 4.465 8.248 W/(Ti+Nb+W ) 0.000 0.000 0.000 0.000 0.000 0.000 0.230 0.000 La+Gd+Y+Yb+Lu 18.868 18.759 18.650 18.868 18.759 18.650 16.592 18.013 Ln number 2 2 2 2 2 2 2 2 Ta/W - - - - - - 3 - Li+ Na+K 1.105 1.106 1.108 1.105 1.106 L108 1.113 1.062 Mg+Ca+Sr+Ba 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 nd 1.88090 1.87969 1.87900 1.88104 1.87996 1.87935 1.87792 1.87864 vd 37.0 37.0 37.0 37.0 37.0 37.0 36.9 36.8 Partial dispersion ratio (eg,f) 0.57623 0.57678 0.57618 0.57665 0.57738 0.57780 0.57587 0.57782 Intercept b (a=0.00250) 0.66873 0.66928 0.66868 0.66915 0.66988 0.67030 0.66812 0.66982 Tg(°C) 611 AtfC) 658 λ8〇[ηηι] 503.5 425.5 439.5 449.5 435.5 425.5 441 λ7〇[ηηι] 383 382 379 382 386.5 382.5 377 382.5 λ5[ηηι] 343 343.5 343.5 343 343.5 343.5 337.5 345.5 Liquidus temperature (°c) 1,080 1,080 1,100 1,080 1,120 1,100 1,120 1,080 -36- 159312. Doc 201223907 [Table 5] Example 33 34 35 36 37 38 39 40 B2O3 34.950 32.807 33.997 31.394 30.148 33.795 31.438 31.482 La2〇3 18.083 17.407 17.824 17.469 14.083 16.835 16.117 14.760 W〇3 Ti02 4.165 4.585 1.800 Nb205 4.327 4.033 2.128 2.253 4.442 2.256 2.259 Li20 1.166 1.145 1.114 1.047 1.143 1,107 1.049 1.050 Gd2〇3 1.357 2.051 1.197 1.274 5.374 1.190 2.513 3.756 y2〇3 Yb2〇3 Lll2〇3 T&amp;2〇5 4.916 4.233 4.446 5.680 5.155 3.769 5.688 5.696 Si02 5.508 6.731 5.104 7.102 6.121 6.5 10 7.112 7.122 Na20 K20 MgO CaO SrO BaO P2〇5 Zr02 5.440 5.225 5.084 6.628 6.095 5.054 6.637 6.646 ZnO 24.255 26.367 24.942 27.152 27.297 25.500 27.190 27.228 Ga2〇3 Sb203 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ti+Nb+W 4.327 4.033 6.293 2.253 4.585 6.242 2.256 2.259 Ti+Nb 4.327 4.033 6.293 2.253 4.585 6.242 2.256 2.259 W/(Ti+Nb+W) 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 La+G d+Y+Yb+Lu 19.439 19.458 19.021 18.743 19.456 18.025 18.630 18.517 Ln number 2 2 2 2 2 2 2 2 Ta/W - - - - - - - - Li + Na + K 1.166 1.145 1.114 1.047 1.143 1.107 1.049 1.050 Mg+Ca+Sr+Ba 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 nd 1.88089 1.87684 1.87927 1.87746 1.88105 1.87840 1.87649 1.87600 vd 37.9 38.3 37.5 38.7 38.3 37.1 38.7 38.7 Partial dispersion ratio (eg,f) 0.57370 0.57255 0.57509 0.57061 0.57298 0.57590 0.57067 0.57048 Intercept b (a=0.00250) 0.66845 0.66830 0.66884 0.66736 0.66873 0.6686 5 0.66742 0.66723 TgCC) At(°C) λ8〇[ηηι] 436 440 527.5 458 447.5 439.5 442 439 λ7〇[ητη] 375 377 384 379 383 3S0 374.5 374.5 λ5[ηηι] 323.5 322 342 318 341 337 318 318.5 Liquid phase Temperature (°c) 1,120 1,140 1,120 1,140 1,150 1,110 1,110 1,110 37- 159312.doc 201223907 [Table 6] Example 41 42 43 44 45 46 47 48 B203 39.683 33.465 31.692 34.137 33.676 33.447 33.491 32.283 L^2〇3 17.839 17.545 17.053 18.957 18.953 17.535 16.246 17.682 W03 Ti02 4.168 2.115 3.649 4.126 4.125 5.879 5.886 5.928 Nb2〇5 3.219 2.829 1.103 3.144 3.175 1.558 1.560 Li20 1.114 1.096 1.022 1.103 1.103 1.096 1.097 1.105 Gd2〇3 1.198 1.179 1.244 1.178 2.359 1.188 y2〇3 Yb203 Lu2〇3 0.018 0.018 Χ3·2〇5 3.794 5.717 5.545 3.756 3.755 4.374 4.380 5.356 Si02 6.447 5.720 5.916 6.487' 6.443 6.452 6.49 Na20 K20 MgO CaO SrO BaO P2O5 0.020 Zr02 5.088 5.004 6.470 5.037 5.036 5.002 5.008 5.043 ZnO 23.895 24.604 26.504 23.796 23.650 23.489 23.520 24.919 Ga2〇3 0.010 Sb2〇3 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ti+Nb+W 7.387 4.943 4.751 7.270 7.301 7.437 7.447 5.928 Ti+Nb 7.387 4.943 4.751 7.270 7.301 7.437 7.447 5.928 W/(Ti+Nb+W) 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 La+Gd+Y+Yb+Lu 19.037 18.723 18.296 18.975 18.971 18.713 18.605 18.869 Ln number 2 2 2 2 2 2 2 2 Ta/W - - - - - - - - Li+Na+K 1.114 1.096 1.022 1.103 1.103 1.096 1.097 1.105 Mg+Ca+Sr+Ba 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 nd 1.88111 1.88185 1.88334 1.88134 1.87826 1.87683 vd 37.1 37.4 37.7 37.1 37.1 37.8 Partial dispersion Ratio (eg,f) 0.57684 0.57513 0.57441 0.57653 0.57710 0.57482 Intercept b(a=0.00250) 0.66959 0.66863 0.66866 0.66928 0.66985 0.66932 Tg(°C) AtfC) λ8〇[ηηι] 442.5 451.5 448 435.5 431.5 442.5 450.5 444.5 λ7〇[ηπι ] 382.5 380.5 382 382.5 381.5 382 384.5 382.5 X5[nm] 343 337 340 343 343 34 5 346 344 Liquidus temperature (°c) 1,120 1,120 1,120 1,100 1,150 1,110 1,100 1,080 159312.doc 38 s 201223907 [Table 7] Example 49 50 51 52 53 54 55 56 B2〇3 32.326 33.725 33.491 33.376 33.695 33.710 33.740 33.280 L&amp ;2〇3 16.382 17.659 16.246 17.498 18.523 18.091 17.226 17.609 W〇3 0.926 Ti02 5.936 4.131 5.886 5.866 4.128 4.129 4.133 4.120 Nb2〇5 3.180 1.560 2.089 3.177 3.179 3.181 2.902 Li20 1.106 1.105 1.097 1.093 1.104 1.104 1.105 1.102 Gd2〇3 2.379 1.188 2.359 1.175 0.396 0.791 1.584 1.184 γ2〇3 Yb203 Lu2〇3 0.018 0.018 0.018 0.018 0.018 Ta2〇5 5.363 3.761 4.380 4.043 3.757 3.759 3.763 3.426 Si02 6.506 6.497 6.452 6.429 6.491 6.494 6.500 6.478 NazO K20 MgO CaO SrO BaO p2〇5 Zr02 5.050 5.043 5.008 4.991 5.039 5.041 5.045 5.029 ZnO 24.953 23.684 23.520 23.439 23.663 23.673 23.694 23.916 Ga2〇3 0.010 0.010 0.010 0.010 0.010 Sb203 Total 100.00 100.00 100.00 100. 00 100.00 100.00 100.00 100.00 Ti+Nb+W 5.936 7.311 7.447 7.955 7.305 7.308 7.315 7.947 Ti+Nb 5.936 7.311 7.447 7.955 7.305 7.308 7.315 7.021 W/(Ti+Nb+W) 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.117 La+Gd+ Y+Yb+Lu 18.761 18.865 18.605 18.673 18.937 18.901 18.828 18.811 Ln number 2 3 2 2 3 3 3 3 TaAV - - - - - - - 4 Li+Na+K 1.106 1.105 1.097 1.093 1.104 1.104 1.105 1.102 Mg+Ca+ Sr+Ba 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 nd 1.87615 1.88051 1.87815 1.88124 1.88106 1.88101 1.88035 1.87946 vd 37.8 37.0 37.1 36.8 37.0 37.0 37.0 36.9 Partial dispersion ratio (eg,f) 0.57574 0.57671 0.57735 0.57769 0.57647 0.57647 0.57671 0.57791 Intercept b(a =0.00250) 0.67024 0.66921 0.67010 0.66969 0.66897 0.66897 0.66921 0.67016 Tg(°C) At(°C) λ8〇[ηπι] 453 437 438 438.5 431 434.5 436 430.5 λ7〇[ηηι] 383.5 384.5 383 383 383 384 384.5 383.5 λ5[ηιτι ] 344.5 343.5 345.5 346 343 343 343.5 345 Liquidus temperature (°c) 1,080 1,080 1,080 1,090 1,090 1,080 1,080 1,080 39- 159 312.doc 201223907 [Table 8] Example 57 58 59 60 61 62 63 64 B2O3 33.725 33.138 33.148 33.631 33.203 33.236 33.170 33.577 La2〇3 17.659 17.731 17.984 18.051 17.645 18.902 17.748 17.977 W〇3 1.000 0.963 1.261 1.076 0.990 0.925 0.821 1.153 Ti02 2.531 4.148 2.506 1.469 4.128 4.114 4.152 2.523 Nb2〇5 3.780 2.547 3.239 4.078 2.692 2.898 2.691 3.232 Li20 1.105 1.109 1.125 1.129 1.104 1.100 1.110 1.125 Gd2〇3 1.188 1.193 1.008 0.688 1.187 1.194 1.008 y2〇3 Yb203 L112O3 0.018 0.018 0.018 0.018 0.018 0.018 0.018 Ta2〇5 3.761 3.776 3.830 3.844 3.531 3.422 3.780 3.829 Si02 6.497 6.523 6.616 6.641 6.014 6.470 6.434 6.103 Na20 K20 MgO CaO SrO BaO p2〇5 Zr02 5.043 5.064 5.136 5.155 5.039 5.022 5.069 5.336 ZnO 23.684 23.780 24.119 24.210 24.440 23.884 23.803 24.110 Ga2〇 3 0.010 0.010 0.010 0.010 0.010 0.010 0.010 0.010 Sb2〇3 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 10 0.00 Ti+Nb+W 7.311 7.659 7.005 6.623 7.809 7.937 7.665 6.908 Ti+Nb 6.311 6.695 5.745 5.547 6.820 7.012 6.844 5.755 W/(Ti+Nb+W) 0.137 0.126 0.180 0.162 0.127 0.117 0.107 0.167 La+Gd+Y+Yb+ Lu 18.865 18.941 19.010 18.757 18.849 18.920 18.960 19.003 Ln number 3 3 3 3 3 2 3 3 Ta/W 4 4 3 4 4 4 5 3 Li+Na+K 1.105 1.109 1.125 1.129 1.104 1.100 1.110 1.125 Mg+Ca+Sr+ Ba 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 nd 1.88076 1.87953 1.87984 1.87935 1.88051 1.87994 1.87957 1.88022 vd 36.9 37.1 37.2 37.2 37.0 37.0 37.0 37.2 Partial dispersion ratio (0g, F) 0.57676 0.57733 0.57632 0.57590 0.57647 0.57762 0.57780 0.57657 Intercept b (a=0.00250 0.66901 0.67008 0.66932 0.66890 0.66897 0.67012 0.67030 0.66957 Tg(0C) At(°C) λ8〇[ηηι] 430.5 429.5 436 431 445.5 448 453.5 418.5 λ7〇[ηηι] 380 381 381 379 386 388 388.5 377 λ5[ηηι] 342.5 344.5 343 340 345 345.5 345.5 342.5 Liquidus temperature (°c) 1,100 1,080 1,080 1,120 1,080 1,080 1,080 1,080 •40- 159312.doc 201223907 [Table 9] Example 65 66 67 68 69 70 71 72 B2〇3 33.164 33.248 32.180 30.609 32.841 33.258 33.131 32.513 La2〇3 19.065 17.992 18.539 18.196 18.399 18.036 18.003 18.582 W〇3 1.151 0.996 2.788 2.520 2.257 1.264 0.944 1.465 Ti02 2.519 2.507 2.513 2.503 Nb2〇 5 3.226 3.471 3.338 3.236 4.084 3.247 3.235 3.330 Li20 1.123 1.125 1.160 1.124 1.151 1.128 1.124 1.157 Gd2〇3 1.008 1.039 0.619 1.059 1.063 0.958 Y203 Yb2〇3 L1I2O3 0.018 0.018 0.019 0.018 0.019 0.018 0.018 0.019 T&amp;2〇5 3.822 3.832 3.948 3.827 3.919 3.840 3.826 4.405 Si02 6.505 6.522 6.820 6.612 6.769 6.292 6.025 6.054 Na20 K20 MgO CaO SrO BaO P2〇5 Zr02 5.326 5.138 5.294 5.132 5.255 5.150 5.130 5.282 ZnO 24.069 24.131 24.864 28.716 24.677 24.184 24.988 26.226 Ga2〇3 0.010 0.010 0.010 0.010 0.010 0.010 0.010 0.010 Sb2〇3 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ti+Nb+W 6.897 6.975 6.126 5.756 6.341 7 .024 6.682 4.796 Ti+Nb 5.745 5.978 3.338 3.236 4.084 5.760 5.738 3.330 W/(Ti+Nb+W) 0.167 0.143 0.455 0.438 0.356 0.180 0.141 0.306 La+Gd+Y+Yb+Lu 19.084 19.019 19.597 18.214 19.037 19.114 19.084 19.558 Ln number 2 3 3 2 3 3 3 3 Ta/W 3 4 1 2 2 3 4 3 Li+Na+K 1.123 1.125 1.160 1.124 1.151 1.128 1.124 1.157 Mg+Ca+Sr+Ba 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 1.88064 1.88091 1.88152 1.88062 1.88184 1.88133 1.88108 1.88055 vd 37.2 37.1 37.5 37.4 37.3 37.1 37.2 37.9 Partial dispersion ratio (eg,f) 0.57608 0.57631 0.57429 0.57647 0.57583 0.57576 0.57608 0.57426 Intercept b (a=0.00250) 0.66908 0.66906 0.66804 0.66997 0.66908 0.66851 0.66908 0.66901 TgCC) ACC) λ8〇[ηηι] 433 423.5 428.5 424.5 424 433 438.5 427 λ7〇[ηηι] 378.5 377 377.5 377 377 382.5 381.5 376 λ5[ηηι] 342.5 342 341.5 340.5 340 343 342 336.5 Liquidus temperature (°c) 1,080 1,100 1,100 1,100 1,100 1,080 1,100 1,100 • 41 · 159312.doc 201223907 [Table 〇] Example 73 74 75 76 77 78 79 80 B2〇3 33,206 32.890 31.722 30.781 31.712 32.378 32.149 32.152 L^2〇3 18.010 18.284 18.857 17.758 18.395 18.405 18.600 18.730 W〇3 1.153 2.564 2.801 2.522 2.627 2.581 2.637 2.642 Ti02 2.522 Nb2〇5 3.230 3.572 3.293 3.239 3.292 3.314 3.304 3.311 Li20 1.124 1.144 1.144 1.125 1.144 1.151 1.148 1.150 1.150 Gd203 0.870 Y2〇3 Yb203 Lll2〇3 0.018 0.019 0.019 0.018 0.019 0.019 0.019 0.019 Ta2〇5 3.910 4.355 3.979 4.161 4.314 4.647 4.329 4.338 Si02 6.514 6.727 6.728 6.617 6.726 6.771 6.750 6.764 Na20 K20 MgO CaO SrO BaO p2〇5 Zr02 5.333 5.222 5.223 5.137 5.546 5.305 5.567 5.433 ZnO 24.100 25.215 26.225 28.632 26.216 25.419 25.487 25.449 Ga2〇3 0.010 0.010 0.010 0.010 0.010 0.010 0.010 0.010 Sb203 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ti+Nb+W 6.905 6.136 6.094 5.761 5.919 5.895 5.941 5.953 Ti+Nb 5.753 3.572 3.293 3.239 3.292 3.314 3.304 3.311 W/(Ti+Nb+W) 0. 167 0.418 0.460 0.438 0.444 0.438 0.444 0.444 La+Gd+Y+Yb+Lu 18.898 18.302 18.876 17.776 18.414 18.423 18.618 18.749 Ln number 3 2 2 2 2 2 2 2 Ta/W 3 2 1 2 2 2 2 2 Li+Na +K 1.124 1.144 1.144 1.125 1.144 1.151 1.148 1.150 Mg+Ca+Sr+Ba 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 nd 1.88128 1.87948 1.88103 1.87983 1.88151 1.88045 1.88201 1.88221 vd 37.1 37.3 37.4 37.3 37.3 37.3 37.3 37.4 Partial dispersion ratio (eg, f 0.57600 0.57560 0.57513 0.57567 0.57487 0.57560 0.57621 0.57621 Intercept b (a=0.00250) 0.66875 0.66885 0.66863 0.66892 0.66812 0.66885 0.66946 0.66971 Tg(°C) 607 606 At(°C) 657 654 λ8〇[ηιη] 439 433 428.5 436.5 436.5 432 432.5 429 λ7〇[ηιη] 382 379.5 379 381 381.5 380 379.5 379 λ5[ηιη] 343 341.5 341.5 341 341.5 341.5 341.5 341.5 Liquidus temperature (°c) 1,080 1,080 1,100 1,100 1,100 1,080 1,100 1,100 159312.doc -42-

201223907 [Table 11] Example 81 82 83 B2〇3 32.376 31.897 33.293 La2〇3 18.312 18.204 18.866 W〇3 2.645 2.621 1.149 Ti02 2.515 Nb2〇5 3.314 3.402 3.221 Li2〇1.151 1.141 1.121 Gd2〇3 Y2〇3 Yb2〇3 Lli2〇3 0.019 0.019 0.018 Ta205 4.681 4.304 3.898 Si02 6.771 6.711 6.567 Na2〇K20 MgO CaO SrO BaO P2〇5 Zr02 5.304 5.534 5.317 ZnO 25.418 26.158 24.027 Ga2〇3 0.010 0.010 0.010 Sb2〇3 Total 100.00 100.00 100.00 Ti+Nb+W 5.959 6.023 6.884 Ti+Nb 3.314 3.402 5.735 W/(Ti+Nb+W) 0.444 0.435 0.167 La+Gd+Y+Yb+Lu 18.330 18.222 18.885 Ln number 2 2 2 Ta/W 2 2 3 Li+Na+K 1.151 1.141 1.121 Mg+Ca+Sr+Ba 0.000 0.000 0.000 nd 1.88108 1.88186 1.88157 Vd 37.2 37.2 37.2 Partial dispersion ratio (eg,f) 0.57541 0.57546 0.57564 Intercept b(a=0.00250) 0.66841 0.66846 0.66864 Tg(°C) At( °C) λ8〇[ηιτι] 426.5 435 429 λ7〇[ηΓη] 379.5 381 379 λ5[ηπι] 342 342 341.5 Liquidus temperature (°c) 1,080 1,080 1,080 -43- 159312.doc 201223 907 [Table 12] Example 84 85 86 87 88 89 90 91 B2〇3 32.802 34.526 34.649 33.534 33.650 33.745 33.120 34.514 L&amp;2〇3 18.482 19.454 18.166 18.895 17.642 19.014 18.662 17.130 W〇3 1.356 Ti02 8.578 4.108 4.122 3.235 5.821 Nb2 〇5 5.643 5.664 4.247 4.261 4.543 3.664 5.641 Li20 0.981 1.131 1.135 1.098 1.102 1.105 1.085 1.130 Gd203 Y2〇3 Yb203 Lll2〇3 Ta2〇5 4.637 3.185 4.198 3.094 4.077 3.113 3.056 4.181 Si02 6.319 6.651 6.675 6.460 6.482 6.501 6.380 6.649 Na20 K20 MgO CaO SrO BaO P2〇5 Zr02 5.132 5.163 5.181 5.015 5.032 5.046 4.953 5.161 ZnO 23.070 24.247 24.333 23.550 23.631 23.698 23.259 24.238 Ga2〇3 Sb203 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ti+Nb+W 8.578 5.643 5.664 8.354 8.383 7.778 9.485 6.997 Ti +Nb 8.578 5.643 5,664 8,354 8.383 7.778 9.485 5.641 W/(Ti+Nb+W) 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.194 La+Gd+Y+Yb+Lu 18.482 19.454 18.166 18.895 17.642 19.014 18.662 17.130 with Ln number 1 1 1 1 1 1 1 1 Ta/W - - - - - - - 3.084 Li+Na+K 0.981 1.131 1.135 1.098 1.102 1.105 1.085 1.130 Mg+Ca+Sr+Ba 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 nd 1.88190 1.87849 1.88124 1.88585 1.88809 1.88450 1.88875 1.88179 vd 36.7 37.7 37.0 36.4 35.8 36.6 35.9 36.3 Partial dispersion ratio (eg,f) 0.57844 0.57523 0.57550 0.57789 0.57920 0.57746 0.58003 0.57743 Intercept b (a=0.00250) 0.67019 0.66948 0.66800 0.66889 0.66870 0.66896 0.66978 0.66818 Tg(0C) ACC) λ8〇[ηηι] 472 519.5 500.5 528 448 430.5 431 415.5 λ70[ηηι] 386 389 372 393 385 376.5 379.5 372 X5[ Nm] 347 324.5 325.5 342 343.5 339.5 344.5 337 Liquidus temperature (°c) 1,120 1,160 1,120 1,080 1,080 1,110 1,080 1,100 44- 159312.doc 201223907 [Table 13] Example 92 93 94 95 96 97 98 99 B2〇3 34.514 33.678 34.494 33.201 32.717 33.332 32,343 33.882 La2〇3 17.130 18.976 19.435 18.707 18.434 18.781 18.224 16.816 W〇3 1.331 T I02 1.360 4.126 4.225 4.067 7.493 5.858 5.685 Nb2〇5 5.641 3.186 4.368 3.141 3.095 2.086 2.542 4.453 Li20 1.130 1.103 1.130 1.087 1.072 1.092 1.059 1.110 Gd2〇3 Y2〇3 Yb2〇3 L\l2〇3 Ta2〇5 4.181 3.756 4.288 3.383 3.018 4.038 2.984 4.105 Si02 6.649 6.488 6.645 6.396 6.303 6.421 6.231 4.127 Na20 K20 MgO CaO SrO BaO P2〇5 Zr02 5.161 5.036 1.191 4.965 4.892 4.984 4.837 5.067 ZnO 24.238 23.651 24.224 25.052 22.976 23.408 26.096 29.109 Ga2〇3 Sb2〇3 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ti+Nb+W 7.001 7.312 8.593 7.208 10.588 7.945 8.227 5.784 Ti+Nb 7.001 7.312 8.593 7.208 10.588 7.945 8.227 4.453 W/(Ti+Nb+W) 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.230 La+Gd+Y +Yb+Lu 17.130 18.976 19.435 18.707 18.434 18.781 18.224 16.816 Ln number 1 1 1 1 1 1 1 1 Ta/W - - - - _ - - 3.084 Li+Na+K 1.130 1.103 1.130 1.087 1.072 1.092 1.059 1.110 Mg+Ca+Sr+Ba 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 nd 1.88400 1.88131 1.88299 1.87958 1.89146 1.88197 1.88016 1.87970 vd 36.1 37.0 36.3 37.2 35.5 36.8 36.8 36.9 Partial dispersion ratio (eg,f) 0.57721 0.57671 0.57864 0.57668 0.57853 0.57776 0.57665 Intercept b(a=0.00250) 0.66746 0.66921 0.66939 0.66968 0.67053 0.66976 0.66890 Tg(°C) A(C) λ8〇[ηηι] 418 432 443 431 437.5 432 431 423 λ7〇[ηιη] 372.5 378.5 382 376.5 383.5 379.5 380 377 λ5[ Ηηι] 336 342 344 341.5 348 345 344.5 337 Liquidus temperature (°c) 1,100 1,080 1,100 1,080 1,080 1,080 1,100 3,100 -45- 159312.doc 201223907 [Table 14] Example 100 101 102 103 104 105 B2O3 33.996 31.349 33.226 33.403 33.291 32.376 La2〇3 19.568 18.860 18.495 18.821 18.888 18.427 W〇3 1.149 2.580 Ti02 8.234 5.871 2.514 Nb205 3.865 2.250 1.556 3.220 3.314 Li20 1.157 1.046 0.982 1.094 1.121 1.151 Gd2〇3 Y2〇3 Yb203 Lll2〇3 Ta2〇5 4.909 5.672 4.640 4.368 3.897 4.647 Si〇2 6. 690 7.092 5.858 6.435 6.566 6.771 Na20 K20 MgO CaO SrO BaO P2〇5 Zr02 5.433 6.618 5.135 4.995 5.317 5.304 ZnO 24.382 27.113 23.429 23.458 24.026 25.418 Ga2〇3 Sb203 0.010 0.010 Total 100.00 100.00 100.00 100.00 100.00 100.00 Ti+Nb+W 3.865 2.250 8.234 7.427 6.884 5.895 Ti+Nb 3.865 2.250 8.234 7.427 5.735 3.314 W/(Ti+Nb+W) 0.000 0.000 0.000 0.000 0.167 0.438 La+Gd+Y+Yb+Lu 19.568 18.860 18.495 18.821 18.888 18.427 with Ln number 1 1 1 1 1 1 Ta/W - - - - 3.392 1.801 Li+Na+K 1.157 1.046 0.982 1.094 1.121 1.151 Mg+Ca+Sr+Ba 0.000 0.000 0.000 0.000 0.000 0.000 na 1.87841 1.87790 1.87976 1.88144 1.88177 vd 38.2 38.7 37.2 37.2 37.3 Partial dispersion ratio ( 0g,F) 0.57224 0.57055 0.57710 0.57637 0.57608 Intercept b(a=0.00250) 0.66774 0.66730 0.67010 0.66937 0.66933 Tg(°C) At(°C) λ8〇[ηΓη] 446 465.5 452 440 429.5 λ7〇[ηπι] 386 388 397.5 386 383.5 381.5 λ5[ΠΓΠ] 322.5 318.5 348 345 343 342 Liquid temperature (°c) 1,100 1,110 1,100 1,120 1,080 1,080 159312.doc -46- 201223907 As shown in Tables 1 to 14, 'the optical glass of the embodiment of the present invention has a liquidus temperature of 1200 ° C or less', in more detail Below 1160 ° C, within the desired range. On the other hand, the liquid phase temperature of the glass of Comparative Example (No. A) was higher than 1200C. The reason why the liquidus temperature is different as described above is that the optical glass of the embodiment of the present invention is different from the comparative example (No. A) and contains a Ti 2 component, a W 3 component, and a Ν 〇 5 component. At least one aspect of it. Therefore, it is understood that the optical glass of the embodiment of the present invention has a lower liquidus temperature than the comparative example (N〇 A). Further, the optical glass having a transmittance of 7〇% in the embodiment of the present invention is 45 nm or less, and more specifically 4 13 nm or less. Further, the wavelength of the optical glass system according to the embodiment of the present invention is 5% or less, and more specifically 361 nm or less. Further, the optical glass system (wavelength at a transmittance of 80%) of the embodiment of the present invention is 550 nm or less', and more specifically 530 nm or less. Therefore, it is understood that the optical glass of the embodiment of the present invention has a high transmittance at a short wavelength of visible light and is difficult to color. Further, the optical glass-based glass transition point (Tg) of the examples of the present invention is 680 ° C or lower, and more specifically 630. (The following is within the desired range. Further, the optical glass-based deformation point (At) of the embodiment (No. 8) of the present invention is 720 C or less, and more specifically 080 ° C or less, as expected. Further, the optical glass of the embodiment of the present invention has a refractive index (nd) of 175 or more, more specifically 1.85 or more, and the refractive index (nd) is 195 or less, and more specifically 1.91. In the following, it is within the range of the desired range. 159312.doc -47·201223907 Further, the optical glass of the embodiment of the present invention has an Abbe number (Vd) of 30 or more, more specifically 31 or more, and the Abbe The number "is less than 5 inches, more detailed and § is below 41" is within the desired range. Further, the optical glass system partial dispersion ratio (0g, F) of the embodiment of the present invention is (-2.50&gt;&lt; 103 parent 乂()+0.6571) or more, more specifically (_2.50&gt;&lt;10.3乂vd+0.6672) or more. On the other hand, the partial dispersion ratio of the optical glass of the embodiment of the present invention is (- 2.5〇xl〇.3xVd+〇.6971) Hereinafter, in more detail, it is (-2.5〇xl (T3xvd+〇.6725) or less. Therefore, it is known that The partial dispersion ratio (0g 'F) is within the desired range. Therefore, it can be seen that the refractive index (nd) and the Abbe number (vd) of the optical glass of the embodiment of the present invention are within the range of the desired range, and visible light The transmittance at a short wavelength is higher than that of the 'devitrification resistance, and it is easy to use pressure softening by heat softening.> Further, after reheating and press forming using the optical glass of the embodiment of the present invention, grinding and grinding are performed. Grinding and processing into a shape of a lens and a crucible. Further, the optical preform of the embodiment of the present invention is used to form a preform for precision press molding, and the preform for precision press molding is subjected to precision press forming into a lens and a rib. The shape of the mirror. In either case, the problem of 'whitening and devitrification does not occur on the glass after heating and softening' and can be stably processed into various lenses and shapes of the crucible. The above is explained in detail for the purpose of illustration. The present invention is intended to be illustrative only, and various modifications may be made without departing from the spirit and scope of the invention. -48- 1593I2.doc

Claims (1)

201223907 VII. Patent application scope: 1 · An optical glass whose total mass of glass in terms of oxide conversion composition contains B2〇3 component 10.0~50.0% and La203 component 5,0~3〇.〇 %' and Moer and (Ding 丨〇 2+ 〇 3+ 灿 2 〇 5) The total mass of the glass relative to the oxide conversion composition is 〇. 1~3〇.〇〇/. . 2. The optical glass of claim 1, wherein the content of the total mass of the glass relative to the oxide-converted composition, the content of the WO3 component, is 20.0% or less in terms of mol%. 3* The optical glass of claim 1 wherein the content of the w〇3 component is less than 70% in terms of mol% relative to the total mass of the glass in terms of oxide conversion. 4. The optical glass of claim 1, which further comprises the following components in terms of mol% of the total mass of the glass in terms of oxide conversion: Ti〇2 component 〇20.0% and/or Nb2〇5 component 〇 ~20.0%. 5. The optical glass of claim 4, wherein the molar mass of the molar and (Ti〇2+Nb2〇5) relative to the oxide-converted composition is 2.0% or more and 30.0% or less. 6. The optical glass of claim ,, wherein the molar ratio of the molar ratio w〇3/(Ti〇2+Nb2〇5 + w〇3) is 0.600 or less. 7. The optical glass of the claim ,, wherein the content of the LhO component is 2 〇% or less in terms of mol% with respect to the total mass of the glass in terms of oxide conversion. 8. The optical glass of claim 7, wherein the content of the Li20 component is Q 1% or more in terms of mol% with respect to the total mass of the glass of the oxide conversion composition. 9. In the case of the claim item Xuebo 35, the total mass of the glass relative to the oxide-converted composition further includes the following components in terms of mol%: Gd2〇3 composition 〇~30.0% and/or 159312.doc 201223907 Y2〇3 Ingredient 〇~1〇〇% and/or Yb2〇3 component 〇~1〇·〇% and/or Lu2〇3 component 〇~1〇.〇〇/〇. Ίο. 11. 12. 13. 14. 15. 16. 17. As requested by the optical glass, where the composition of Ln2〇3 (in the formula, free La, Gd, γ, Yb, Lu) The total mass of the surface of the composition of 44% or more and the composition of the oxide is from 1% by mass to 40.0%. For example, the optical glass of the requester contains two or more components of the above-mentioned composition. The content of the Ta205 component of the optical glass of the request, which is the composition of the optical glass in terms of oxide conversion, is 2% or less in terms of mol%. The optical glass of claim 12, wherein the molar ratio Ta205/W〇3 of the oxide conversion composition is 1.〇 or more and ι〇·〇 or less. The SiO2 component is contained in an amount of 25 % by mole or less based on the total mass of the glass of the optical glass of the request. The optical glass of claim 4, wherein the content of the Si 2 component is 19% by mole or less based on the total mass of the glass in terms of oxide conversion composition. The optical glass of claim 1, which comprises the following components in terms of mol% of the total mass of the glass in terms of oxide conversion. Na20 component 〇~15.〇% and/or K2〇 component 〇~1〇. 〇%. The optical glass of claim 16 wherein the RnW component (wherein Rn is selected from the group consisting of U, Na, and K) and the relative 159312.doc -2- 201223907 are converted into oxides. The total mass of the composed glass is below 20%. 18. The optical glass according to the claim ,, which further contains the following components in terms of mole % of the glass in terms of oxide conversion: MgO component 〇~ι〇·〇% and/or 4 CaO component 〇~ 10. 〇% and/or SrO composition 〇~10.0% and/or s BaO composition 〇~1〇.〇〇/0. The optical glass of claim 18, wherein the R 〇 component (where r is one or more selected from the group consisting of Mg, Ca, Sr, and Ba) and the glass in terms of oxides The total mass is below 11%. 20. The optical glass of claim ,, further comprising the following components in terms of mol% of the total weight of the glass in terms of oxide conversion: Ge02 component 〇10.0% and/or P2〇5 component 〇10.0% And / or Zr02 ingredients 0 ~ 150. /. And/or ZnO component 0~5〇〇% and/or Bi2〇3 component 〇~15.0% and/or Te02 component 〇~15〇% and/or ^A12〇3 component 〇15.0% and/or Ga203 component 0 ~15.0% and/or sb2〇3 component 〇~1.0%; and the fluoride which is partially or completely replaced with one or more of the above metal elements is in the range of F 66.〇% . 21. The optical glass of claim ,, having a refractive index of 15975 or more 丨% or less 159312.doc 201223907 rate (nd), and having an Abbe number (vd) of 30 or more and 50 or less. 22. The optical glass of claim 1 which has a glass transition point (Tg) of 680 ° C or less. 23. The optical glass of claim 1 which has a liquid phase temperature of 1250 ° C or less. A pre-formed material comprising the optical glass of any one of claims 1 to 23. 25. An optical element produced by press forming a preform of claim 24. 26. An optical element which is an optical glass according to any one of claims 1 to 23 as a base material. 27. An optical machine having the optical component of claim 25. 28. An optical machine having the optical component of claim 26. 159312.doc 201223907 IV. Designated representative map: (1) The representative representative of the case is: (none) (2) The symbolic symbol of the representative figure is simple: 5. If there is a chemical formula in this case, please reveal the best indication of the characteristics of the invention. Chemical formula: (none) 159312.doc