TW202402695A - Optical glass, preform, and optical element - Google Patents

Abstract

The present invention provides an optical glass, a preform, and an optical element, wherein the optical glass has optical characteristics of high refractive index and high dispersion of color, and the production cost of the glass is low. The optical glass contains, in mass%, more than 0% to 45.0% of a La2O3 component, more than 0% to 45.0% of a TiO2 component, and more than 0% to 40.0% of a BaO component. The total amount of the SiO2 component and the B2O3 component is 5.0% or more and 30.0% or less, the mass ratio of TiO2/(TiO2+BaO) is 0.10 or more and 0.90 or less, the refractive index (nd) is 1.90 or more, the Abbe number ([nu]d) is 30.0 or less, and the wavelength ([lambda]5) indicating the spectral transmittance of 5% is 400 nm or less.

Description

Optical glasses, preforms and optical components

The present invention relates to optical glass, preforms and optical elements.

In recent years, the digitization of machines using optical systems and the improvement of high-definition images and videos have been rapidly developed. In particular, the high-definition of images and videos is extremely noticeable in optical equipment such as digital cameras, video recorders, and projectors. In addition, at the same time, weight reduction and miniaturization can be achieved by reducing the number of optical components, such as lenses or lenses, built into the optical systems of these optical machines.

Among optical glasses for making optical elements, the demand for high refractive index and high dispersion glass with a high refractive index (n _d ) of 1.90 or more and a low Abbe number (ν _d ) of 15.0 or more and 30.0 or less is particularly high, because This kind of optical glass can make the overall optical system lighter and smaller. As such high refractive index and low dispersion glass, a glass composition represented by Patent Document 1 is known. [Prior art documents] [Patent documents]

[Patent Document 1] Japanese Patent Application Publication No. 2011-178571.

[Problem to be solved by the invention]

However, in order to promote high refractive index and high dispersion, the glass described in Patent Document 1 contains a large amount of components with high unit price, such as GeO ₂ components, Nb ₂ O ₅ components, and Ta ₂ O ₅ components, which may increase the production cost. Such problems exist. Therefore, it is desired to have an optical glass that not only has high refractive index/high dispersion, but also has a short wavelength (λ ₅ ) indicating a spectral transmittance of 5% and has low production cost.

In view of the above problems, the object of the present invention is to provide an optical glass that has a high refractive index, a short wavelength (λ ₅ ) indicating a spectral transmittance of 5%, and low production cost, and a preform using the optical glass. with optical components. [Means used to solve problems]

In order to solve the above-mentioned problems, the present inventors concentrated on accumulating the results of experimental studies and found that the total amount of the SiO ₂ component and the B ₂ O ₃ component can be adjusted by using the La ₂ O ₃ component, the TiO ₂ component, and the BaO component together. , or the mass ratio of TiO ₂ / (TiO ₂ + BaO), can obtain the desired high refractive index and high dispersion, and reduce production costs, and the wavelength (λ ₅ ) indicating 5% spectral transmittance is shortened, and it is completed invention. Specifically, the present invention provides the following.

(1) An optical glass containing a La ₂ O ₃ component of more than 0% to 45.0%, a TiO ₂ component of more than 0% to 45.0%, and a BaO component of more than 0% to 40.0% in mass % on an oxide basis ; and the total amount of the SiO ₂ component and the B ₂ O ₃ component is 5.0% or more and 30.0% or less; the mass ratio of TiO ₂ /(TiO ₂ +BaO) is 0.10 or more and 0.90 or less; the refractive index (n _d ) is 1.90 or more , the Abbe number (ν _d ) is 30.0 or less, and the wavelength (λ ₅ ) indicating 5% spectral transmittance is 400 nm or less.

(2) The optical glass as described in (1), wherein the SiO ₂ component is 0% to 30.0%, and the B ₂ O ₃ component is 0% to 30.0% in mass % on an oxide basis.

(3) The optical glass as described in (1) or (2), in which the ZnO component is 0% to 20.0%, Y ₂ O ₃ is 0% to 15.0%, and Nb ₂ O is the mass % of the oxide basis. _{The 5} component is 0% to 25.0%, the Yb ₂ O ₃ component is 0% to 15.0%, and the Gd ₂ O ₃ component is 0% to 15.0%.

(4) The optical glass according to any one of (1) to (3), in which in terms of mass % based on oxide, (La ₂ O ₃ +Nb ₂ O ₅ +Gd ₂ O ₃ +Yb ₂ O ₃ ) The sum of the masses is greater than 0% and less than 60.0%.

(5) The optical glass according to any one of (1) to (4), in which the Ln ₂ O ₃ component (in the formula, Ln is selected from the group consisting of La, Gd, Y, and Yb) is calculated as mass % on an oxide basis. The total amount of more than 1 species in the group is greater than 0% and less than 50.0%.

(6) In the optical glass according to any one of (1) to (5), the mass ratio of TiO ₂ /BaO is greater than 0 and less than 3.00 on an oxide basis.

(7) The optical glass according to any one of (1) to (6), in which the Rn ₂ O component (in the formula, Rn is selected from the group consisting of Li, Na, and K) is calculated as mass % on an oxide basis. The sum of the mass of more than 1 of them) is less than 15.0%.

(8) The optical glass according to any one of (1) to (7), in which the RO component (in the formula, R is selected from the group consisting of Mg, Ca, Sr, Ba, and Zn) is calculated as mass % on an oxide basis. The sum of the masses of more than 1 species in the group is greater than 0% and less than 35.0%.

(9) The optical glass according to any one of (1) to (8), which contains a ZrO ₂ component of 0% to 20.0% and a Nb ₂ O ₅ component of 0% to 15.0% in terms of mass % on an oxide basis. , WO ₃ component 0% to 10.0%, Ta ₂ O ₅ component 0% to 10.0%, MgO component 0% to 15.0%, CaO component 0% to 15.0%, SrO component 0% to 15.0%, Li ₂ O component 0 % to 15.0%, Na ₂ O component 0% to 15.0%, K ₂ O component 0% to 15.0%, P ₂ O ₅ component 0% to 10.0%, GeO ₂ component 0% to 10.0%, Al ₂ O ₃ component 0% to 15.0%, Ga ₂ O ₃ composition 0% to 15.0%, Bi ₂ O ₃ composition 0% to 10.0%, TeO ₂ composition 0% to 10.0%, SnO ₂ composition 0% to 3.0%, and Sb ₂ O ₃ ingredients 0% to 1.0%.

(10) A preform made of the optical glass according to any one of (1) to (9).

(11) An optical element made of the optical glass according to any one of (1) to (9).

(12) An optical machine including the optical element according to (11). [Invention effect]

According to the present invention, it is possible to provide optical glass that not only has a high refractive index but also has a short wavelength (λ ₅ ) indicating a spectral transmittance of 5% and has low production cost, as well as preforms and optical elements using the optical glass.

The optical glass of the present invention contains, in mass %, a La ₂ O ₃ component of greater than 0% to 45.0%, a TiO ₂ component of greater than 0% to 45.0%, and a BaO component of greater than 0% to 40.0%; the SiO ₂ component and B ₂ The total amount of O ₃ components is 5.0% or more and 30.0% or less; the mass ratio of TiO ₂ /(TiO ₂ +BaO) is 0.10 or more and 0.90 or less; the refractive index (n _d ) is 1.90 or more, and the Abbe number (ν _d ) is 30.0 or less, and the wavelength (λ ₅ ) indicating 5% spectral transmittance is 400nm or less. According to the present invention, by adjusting the content of each component while using the La ₂ O ₃ component, the TiO ₂ component, and the BaO component in combination, it is possible to expect a high refractive index and high dispersion of the glass, and to improve the stability of the glass. Therefore, it is possible to provide an optical glass that not only has high refractive index and high dispersion, but also has a short wavelength (λ ₅ ) indicating a spectral transmittance of 5% and has low production cost, as well as preforms and optical elements using the optical glass.

[Glass composition] The composition range of each component constituting the optical glass of the present invention is as follows. In this specification, unless otherwise specified, the content of each component is expressed in mass % relative to the total mass of the glass on an oxide basis. Here, the "oxide standard" refers to the case where all the oxides, complex salts, metal fluorides, etc. used as raw materials for the glass composition components of the present invention are decomposed into oxides during melting. The total mass of is set to 100% by mass to represent the composition of various components contained in the glass.

<About essential components and optional components> The La ₂ O ₃ component is a component that can increase the refractive index of glass and reduce dispersion. In particular, by containing more than 0% of the La ₂ O ₃ component, a desired high refractive index can be obtained, and it is an essential component. Therefore, the lower limit of the content of the La ₂ O ₃ component is preferably greater than 0%, preferably 3.0%, more preferably 15.0%, further preferably 20.0%, still more preferably 25.0%, still more preferably 27.0%. On the other hand, by setting the content of the La ₂ O ₃ component to 45.0% or less, the devitrification resistance of the glass can be improved, the increase in the specific gravity of the glass can be suppressed, and the production cost can be reduced. Therefore, the upper limit of the content of the La ₂ O ₃ component is preferably 45.0%, more preferably 40.0%, more preferably 38.0%, and still more preferably 37.0%. As the La ₂ O ₃ component, La ₂ O ₃ , La(NO ₃ ) ₃ ·XH ₂ O (X is an arbitrary integer), etc. can be used as raw materials.

When the content of the TiO ₂ component is greater than 0%, it is an essential component that can increase the refractive index of the glass, lower the Abbe number, increase the partial dispersion ratio, and improve the devitrification resistance. Therefore, the lower limit of the content of the TiO ₂ component is preferably greater than 0%, preferably 5.0%, more preferably 10.0%, further preferably 15.0%, still more preferably 18.0%, and still more preferably greater than 20.0 %. On the other hand, by setting the content of the TiO ₂ component to 45.0% or less, the coloring of the glass can be reduced and the visible light transmittance can be improved. In addition, devitrification caused by excessive TiO ₂ component content can also be suppressed. Therefore, the upper limit of the content of the TiO ₂ component is preferably 45.0%, more preferably 38.0%, more preferably 32.0%, still more preferably 27.0%, still more preferably 25.0%. TiO ₂ component, TiO ₂ etc. can be used as raw materials.

The BaO component is an essential component that can improve the refractive index or devitrification resistance of the glass and improve the meltability of the glass raw material when the content exceeds 0%. Therefore, the lower limit of the content of the BaO component is preferably greater than 0%, preferably 5.0%, more preferably 8.0%, and still more preferably 10.0%. On the other hand, by setting the content of the BaO component to 40.0% or less, the refractive index of the glass is less likely to decrease and the devitrification of the glass can be reduced. Therefore, the upper limit of the content of the BaO component is preferably 40.0%, more preferably 35.0%, more preferably 28.0%, still more preferably 23.0%, still more preferably 20.0%. As the BaO component, BaCO ₃ , Ba(NO ₃ ) ₂ , etc. can be used as raw materials.

The total content (mass sum) of the B ₂ O ₃ component and the SiO ₂ component is preferably 5.0% or more and 30.0% or less. In particular, by setting the sum to 5.0% or more, it is possible to suppress a decrease in devitrification resistance due to insufficient B ₂ O ₃ components or SiO ₂ components. Therefore, the lower limit of the mass sum (B ₂ O ₃ +SiO ₂ ) is preferably 5.0%, more preferably 7.0%, and more preferably 9.0%. On the other hand, by setting the sum to 30.0% or less, a decrease in the refractive index caused by excessive inclusion of these components can be suppressed, so that a desired high refractive index can be easily obtained. Therefore, the upper limit of the mass sum (B ₂ O ₃ +SiO ₂ ) is preferably 30.0%, more preferably 23.0%, more preferably 18.0%, and still more preferably 16.50%.

Here, the ratio (mass ratio) between the content of the TiO ₂ component and the sum of the contents of the TiO ₂ component and BaO component (mass ratio) is preferably 0.10 or more. In this way, in addition to maintaining a high refractive index and high dispersion, a high partial dispersion ratio can also be obtained. Therefore, the lower limit of the mass ratio TiO ₂ /(TiO ₂ +BaO) is preferably 0.10, more preferably 0.30, more preferably 0.40, and still more preferably 0.45. On the other hand, by setting the mass ratio to 0.90 or less, the coloring of the glass can be reduced, the visible light transmittance can be improved, and devitrification can be suppressed. Therefore, the upper limit of the mass ratio TiO ₂ /(TiO ₂ +BaO) is preferably 0.90, more preferably 0.80, more preferably 0.73, and even more preferably 0.68.

The SiO ₂ component is any component that can improve the devitrification resistance when its content is greater than 0%. Therefore, the lower limit of the content of the SiO ₂ component is preferably greater than 0%, preferably greater than 0.5%, more preferably greater than 1.0%, and still more preferably greater than 2.0%. On the other hand, by setting the content of the SiO ₂ component to 30.0% or less, the SiO ₂ component can be easily melted in the molten glass, thereby eliminating the need for melting at high temperatures. The upper limit of the content of the SiO ₂ component is preferably 30.0%, more preferably 23.0%, more preferably 16.0%, still more preferably 11.0%, still more preferably 9.0%. As the SiO ₂ component, SiO ₂ , K ₂ SiF ₆ , Na ₂ SiF ₆ , etc. can be used as raw materials.

The B ₂ O ₃ component is any component that, when the content exceeds 0%, can form a network structure inside the glass, promote the formation of stable glass, and improve the devitrification resistance. Therefore, the lower limit of the content of the B ₂ O ₃ component is preferably greater than 0%, more preferably greater than 0.5%, more preferably greater than 1.0%, still more preferably greater than 2.0%. On the other hand, by setting the content of the B ₂ O ₃ component to 30.0% or less, a decrease in the refractive index can be suppressed, the Abbe number can be reduced, and deterioration of chemical durability can be suppressed. Therefore, the upper limit of the content of the B ₂ O ₃ component is preferably 30.0% or less, more preferably 20.0%, more preferably less than 15.0%, still more preferably 12.0%, still more preferably less than 10.0%. As the B ₂ O ₃ component, H ₃ BO ₃ , Na ₂ B ₄ O ₇ , Na ₂ B ₄ O ₇・10H ₂ O, BPO ₄ , etc. can be used as raw materials.

The ZnO component is any component that can improve the meltability of glass, lower the glass transition point, and reduce devitrification when its content is greater than 0%. Therefore, the lower limit of the content of the ZnO component is preferably greater than 0%, preferably greater than 0.5%, more preferably greater than 1.0%, and still more preferably greater than 1.5%. On the other hand, by setting the content of the ZnO component to 20.0% or less, reduction in the refractive index and devitrification can be reduced. In addition, since the viscosity of the molten glass can be increased, the occurrence of streaks in the glass can be reduced. Therefore, the upper limit of the content of the ZnO component is preferably 20.0%, more preferably 15.0%, more preferably 11.0%, and still more preferably 8.0%. ZnO component, ZnO, ZnF ₂ , etc. can be used as raw materials.

The Y ₂ O ₃ component is any component that can suppress an increase in the material cost of glass when the content exceeds 0%. By setting the content of the Y ₂ O ₃ component to 15.0% or less, a decrease in the refractive index of the glass can be suppressed, the Abbe number can be reduced, and the devitrification resistance of the glass can be improved. Therefore, the upper limit of the Y ₂ O ₃ component content is preferably 15.0%, more preferably 10.0%, and more preferably 5.0%. Y ₂ O ₃ component, Y ₂ O ₃ , YF ₃ , etc. can be used as raw materials.

The Nb ₂ O ₅ component is any component that can increase the refractive index of glass and improve the devitrification resistance when its content exceeds 0%. Therefore, the lower limit of the content of the Nb ₂ O ₅ component is preferably greater than 0%, preferably 2.0%, and more preferably 4.0%. On the other hand, by setting the content of the Nb ₂ O ₅ component to 25.0% or less, it is possible to suppress a decrease in the devitrification resistance of the glass caused by excessive Nb ₂ O ₅ content, or to suppress a decrease in the transmittance of visible light. , and can suppress the increase in the material cost of glass. Therefore, the upper limit of the content of the Nb ₂ O ₅ component is preferably 25.0%, more preferably 20.0%, more preferably 16.0%, and still more preferably 13.0%. Nb ₂ O ₅ component, Nb ₂ O ₅ , etc. can be used as raw materials.

The Yb ₂ O ₃ component is any component that can increase the refractive index of glass when its content is greater than 0%. On the other hand, by setting the content of the Yb ₂ O ₃ component to 15.0% or less, the devitrification resistance of the glass can be improved and the Abbe number can be reduced. Therefore, the upper limit of the content of the Yb ₂ O ₃ component is preferably 15.0%, more preferably 10.0%, and more preferably 5.0%. Yb ₂ O ₃ component, Yb ₂ O ₃ , etc. can be used as raw materials.

The Gd ₂ O ₃ component is any component that can increase the refractive index of glass and increase the Abbe number when the content exceeds 0%. On the other hand, by reducing the Gd ₂ O ₃ component, which is particularly expensive among rare earth elements, to less than 15.0%, the material cost of the glass can be reduced, and therefore more affordable optical glass can be produced. In addition, this can prevent the Abbe number of the glass from rising higher than necessary. Therefore, the upper limit of the content of the Gd ₂ O ₃ component is preferably 15.0%, more preferably 10.0%, and more preferably 5.0%. Gd ₂ O ₃ component, Gd ₂ O ₃ , GdF ₃ , etc. can be used as raw materials.

In addition, in the optical glass of the present invention, the total content (mass sum) of the La ₂ O ₃ component, the Nb ₂ O ₅ component, the Gd ₂ O ₃ component, and the Yb ₂ O ₃ component is preferably 60.0% or less. Thereby, the content of these expensive components can be reduced, so the material cost of the glass can be suppressed and the Abbe number can be reduced. Therefore, the upper limit of the mass sum (La ₂ O ₃ +Nb ₂ O ₅ +Gd ₂ O ₃ +Yb ₂ O ₃ ) is preferably 60.0%, more preferably 57.0%, more preferably 53.0%, and still more preferably 49.0%, and even better is 47.0%. On the other hand, by containing more than 0% of the mass sum of these components, the desired high refractive index can be obtained. Therefore, the lower limit is preferably greater than 0%, preferably 10.0%, more preferably 20.0%, still more preferably 25.0%, still more preferably 30.0%, still more preferably 35.0%.

The sum of the contents (mass sum) of the Ln ₂ O ₃ component (in the formula, Ln is one or more selected from the group consisting of La, Gd, Y, and Yb) is preferably greater than 0% to 50%. In particular, by setting the mass sum to be greater than 0%, the refractive index of the glass can be increased, so that glass with a high refractive index can be easily obtained. In addition, the staining of the glass can be reduced. Therefore, the lower limit of the mass sum of the content of the Ln ₂ O ₃ component is preferably greater than 0%, more preferably 1.0%, more preferably 3.0%, and still more preferably 5.0%. On the other hand, by setting the mass sum to 50.0% or less, the devitrification resistance can be improved and the Abbe number can be reduced. Therefore, the upper limit of the mass sum of the content of the Ln ₂ O ₃ component is preferably 50.0%, more preferably less than 40.0%, more preferably 30.0%, and still more preferably 25.0%.

Here, the ratio (mass ratio) of the content of the TiO ₂ component to the sum of the contents of the La ₂ O ₃ component, Nb ₂ O ₅ component, Gd ₂ O ₃ component, and Yb ₂ O ₃ component is preferably greater than 0. In this way, in addition to maintaining a high refractive index and high dispersion, a high partial dispersion ratio can also be obtained, and the production cost can be reduced. Therefore, the lower limit of the mass ratio TiO ₂ /(La ₂ O ₃ +Nb ₂ O ₅ +Gd ₂ O ₃ +Yb ₂ O ₃ ) is preferably greater than 0, preferably 0.10, more preferably 0.20, and even better It's 0.40. On the other hand, by setting the mass ratio to 2.00 or less, the coloring of the glass can be reduced, the visible light transmittance can be improved, and devitrification can be suppressed. Therefore, the upper limit of the mass ratio TiO ₂ /(La ₂ O ₃ +Nb ₂ O ₅ +Gd ₂ O ₃ +Yb ₂ O ₃ ) is preferably 2.00, more preferably 1.00, more preferably 0.80, and even more preferably 0.66.

Here, the ratio (mass ratio) of the content of the TiO ₂ component to the content of the BaO component is preferably greater than 0. In this way, in addition to maintaining a high refractive index and high dispersion, a high partial dispersion ratio can also be obtained. The lower limit of the mass ratio TiO ₂ /BaO is preferably greater than 0, more preferably 0.10, more preferably 0.40, still more preferably 0.60. On the other hand, by setting the mass ratio to 3.00 or less, the coloring of the glass can be reduced, the visible light transmittance can be improved, and devitrification can be suppressed. Therefore, the upper limit of the mass ratio TiO ₂ /BaO is preferably 3.00, more preferably 2.00, and more preferably 1.60.

Here, the ratio (mass ratio) of the sum of the contents of the TiO ₂ component and the WO ₃ component to the BaO component is preferably greater than 0. In this way, in addition to maintaining a high refractive index and high dispersion, a high partial dispersion ratio can also be obtained, and the devitrification resistance can be improved. Therefore, the lower limit of the mass ratio (TiO ₂ +WO ₃ )/BaO is preferably greater than 0, preferably 0.30, more preferably 0.60, still more preferably 0.80, still more preferably 1.00. On the other hand, by setting the mass ratio to 3.00 or less, the coloring of the glass can be reduced, the visible light transmittance can be improved, and devitrification can be suppressed. Therefore, the upper limit of the mass ratio (TiO ₂ +WO ₃ )/BaO is preferably 3.00, more preferably 2.50, and more preferably 1.90.

The total content (mass sum) of the TiO ₂ component and the Nb ₂ O ₅ component is preferably greater than 0%. This can increase the refractive index/dispersion of the glass and improve the devitrification resistance. Therefore, the lower limit of the mass sum (TiO ₂ +Nb ₂ O ₅ ) is preferably greater than 0%, preferably greater than 10.0%, more preferably greater than 15.0%, still more preferably greater than 20.0%, still more preferably greater than 25.0%. On the other hand, by setting the mass sum to 60.0% or less, the coloring of the glass can be reduced, the visible light transmittance can be improved, and devitrification can be suppressed. Therefore, the upper limit of the mass sum (TiO ₂ +Nb ₂ O ₅ ) is preferably 60.0%, preferably less than 50.0%, more preferably 45.0%, more preferably 40.0%, and still more preferably 35.0%, Even better is 33.0%.

The total amount of the Rn ₂ O component (in the formula, Rn is one or more selected from the group consisting of Li, Na, K, and Cs) is preferably 15.0% or less. Thereby, it is possible to suppress a decrease in the refractive index of the glass and improve the devitrification resistance. Therefore, the upper limit of the mass sum of the Rn ₂ O component is preferably 15.0%, more preferably 10.0%, more preferably less than 5.0%, still more preferably less than 1.0%.

The total content (mass sum) of the RO components (in the formula, R is one or more selected from the group consisting of Mg, Ca, Sr, and Ba) is preferably 35.0% or less. This can reduce devitrification caused by excessive RO component content and suppress a decrease in the refractive index. Therefore, the upper limit of the mass sum of the RO component content is preferably 35.0%, more preferably 30.0%, more preferably 27.0%, more preferably less than 23.0%, and still more preferably 20.0%. On the other hand, by setting the mass sum to be greater than 0%, the meltability of the glass raw material or the stability of the glass can be improved. Therefore, the lower limit of the total content of RO components is preferably greater than 0%, more preferably 4.0%, more preferably 7.0%, and still more preferably greater than 9.0%.

The ZrO ₂ component is any component that contributes to high refractive index and low dispersion of glass and can improve the devitrification resistance of glass when its content exceeds 0%. Therefore, the lower limit of the content of the ZrO ₂ component is preferably greater than 0%, preferably 0.5%, and more preferably 1.0%. On the other hand, by setting the ZrO ₂ component to 20.0% or less, it is possible to suppress a decrease in the devitrification resistance of the glass or an increase in the Abbe's number from being higher than necessary due to the excessive ZrO ₂ component content. Therefore, the upper limit of the content of the ZrO ₂ component is preferably 20.0%, more preferably 16.0%, more preferably 12.0%, still more preferably 9.0%, and still more preferably less than 6.5%. As a ZrO ₂ component, ZrO ₂ , ZrF ₄ , etc. can be used as raw materials.

When the content of the WO ₃ component is greater than 0%, in addition to reducing the coloring of the glass caused by other high refractive index components, it can also increase the refractive index, increase the partial dispersion ratio, and improve the devitrification resistance of the glass. Any ingredients. In addition, the WO ₃ component is also a component that can lower the glass transition point. Therefore, the lower limit of the content of the WO ₃ component is preferably greater than 0%, preferably 0.1%, more preferably 0.2%, and still more preferably 0.3%. On the other hand, by setting the content of the WO ₃ component to 10.0% or less, glass coloring caused by the WO ₃ component can be reduced and the visible light transmittance can be improved. Therefore, the upper limit of the content of the WO ₃ component is preferably 10.0%, more preferably 5.0%, and more preferably 3.0%. As the WO ₃ component, WO ₃ and the like can be used as raw materials.

The Ta ₂ O ₅ component is any component that can increase the refractive index of the glass and improve the devitrification resistance when the content is greater than 0%. On the other hand, by reducing the expensive Ta ₂ O ₅ component to less than 10.0%, the material cost of the glass can be reduced, and therefore more affordable optical glass can be produced. In addition, by setting the content of the Ta ₂ O ₅ component to 10.0% or less, the melting temperature of the raw material can be lowered and the energy required for melting the raw material can be reduced. Therefore, the manufacturing cost of optical glass can also be reduced. Therefore, the upper limit of the content of the Ta ₂ O ₅ component is preferably 10.0%, more preferably 8.0%, and more preferably 5.0%. Especially from the viewpoint of producing cheaper optical glass, the upper limit of the content of the Ta ₂ O ₅ component is preferably 4.0%, more preferably 3.0%, further preferably less than 1.0%, and most preferably no contain. Ta ₂ O ₅ component, Ta ₂ O ₅ , etc. can be used as raw materials.

The MgO component is any component that can improve the meltability of the glass raw material or the devitrification resistance of the glass when its content exceeds 0%. On the other hand, by setting the content of the MgO component to 15.0% or less, it is possible to suppress a decrease in the refractive index or a decrease in devitrification resistance caused by excessive inclusion of these components. Therefore, the upper limit of the content of the MgO component is preferably 15.0%, more preferably 10.0%, and more preferably 5.0%. For the MgO component, MgCO ₃ , MgF ₂ , etc. can be used as raw materials.

The CaO component is any component that can improve the refractive index or devitrification resistance of the glass and improve the meltability of the glass raw material when the content exceeds 0%. Therefore, the lower limit of the content of the CaO component is preferably greater than 0%, preferably 0.5%, more preferably 1.5%, and still more preferably 3.0%. On the other hand, by setting the content of the CaO component to 15.0% or less, the refractive index of the glass is less likely to decrease and the devitrification of the glass can be reduced. Therefore, the upper limit of the content of the CaO component is preferably 15.0%, more preferably 10.0%, and more preferably 5.0%. As a CaO component, CaCO ₃ , CaF ₂ , etc. can be used as raw materials.

The SrO component is any component that can improve the refractive index or devitrification resistance of the glass and improve the meltability of the glass raw material when the content is greater than 0%. Therefore, the lower limit of the content of the SrO component is preferably greater than 0%, preferably 0.5%, more preferably 1.5%, and still more preferably 3.0%. On the other hand, by setting the content of the SrO component to 15.0% or less, the refractive index of the glass is less likely to decrease and the devitrification of the glass can be reduced. Therefore, the upper limit of the SrO component content is preferably 15.0%, more preferably 10.0%, and more preferably 5.0%. As the SrO component, SrCO ₃ and SrF ₂ can be used as raw materials.

The Li ₂ O component, the Na ₂ O component, and the K ₂ O component are any components that can improve the meltability of the glass when the content of at least any one of them exceeds 0%. In particular, the K ₂ O component is also a component that can further increase the partial dispersion ratio of glass. On the other hand, by reducing the content of the Li ₂ O component, the Na ₂ O component, or the K ₂ O component, a decrease in the refractive index of the glass can be suppressed and devitrification can be reduced. In particular, by reducing the content of the Li ₂ O component, a decrease in the partial dispersion ratio of the glass can be suppressed. Therefore, the content of at least one of the Li ₂ O component, the Na ₂ O component and the K ₂ O component is preferably 15.0% or less, more preferably less than 10.0%, more preferably less than 5.0%, and more preferably Preferably it is less than 1.0%. As the Li ₂ O component, Na ₂ O component and K ₂ O component, Li ₂ CO ₃ , LiNO ₃ , LiF, Na ₂ CO ₃ , NaNO ₃ , NaF, Na ₂ SiF ₆ , K ₂ CO ₃ , KNO ₃ , can be used. KF, KHF ₂ , K ₂ SiF ₆ , etc. are used as raw materials.

The P ₂ O ₅ component is any component that can improve the devitrification resistance of glass when its content is greater than 0%. In particular, by setting the content of the P ₂ O ₅ component to 10.0% or less, it is possible to suppress a decrease in the chemical durability of the glass, especially a decrease in the water resistance. Therefore, the upper limit of the content of the P ₂ O ₅ component is preferably 10.0%, more preferably 5.0%, and more preferably 3.0%. As the P ₂ O ₅ component, Al(PO ₃ ) ₃ , Ca(PO ₃ ) ₂ , Ba(PO ₃ ) ₂ , BPO ₄ , H ₃ PO ₄ , etc. can be used as raw materials.

The GeO ₂ component is any component that can increase the refractive index of glass and improve the devitrification resistance when the content is greater than 0%. However, since the raw material of GeO ₂ is expensive, if it is used in large amounts, the material cost will increase, which will undermine the cost reduction effect brought about by reducing the Gd ₂ O ₃ component or Ta ₂ O ₅ component. Therefore, the upper limit of the content of the GeO ₂ component is preferably 10.0%, more preferably 5.0%, more preferably 1.0%, and most preferably none. GeO ₂ component, GeO ₂ etc. can be used as raw materials.

The Al ₂ O ₃ component and the Ga ₂ O ₃ component are any components that can improve the chemical durability of the glass and improve the devitrification resistance of the glass when the content exceeds 0%. On the other hand, by setting the content of each of the Al ₂ O ₃ component and the Ga ₂ O ₃ component to 15.0% or less, it is possible to suppress a decrease in the devitrification resistance of the glass caused by excessive inclusion of these components. Therefore, the upper limit of the respective contents of the Al ₂ O ₃ component and the Ga ₂ O ₃ component is preferably 15.0%, more preferably 8.0%, and more preferably 3.0%. The Al ₂ O ₃ component and the Ga ₂ O ₃ component can use Al ₂ O ₃ , Al(OH) ₃ , AlF ₃ , Ga ₂ O ₃ , Ga(OH) _3, etc. as raw materials.

The Bi ₂ O ₃ component is any component that can increase the refractive index and lower the glass transition point when the content exceeds 0%. On the other hand, by setting the content of the Bi ₂ O ₃ component to 10.0% or less, the devitrification resistance of the glass can be improved, the coloring of the glass can be reduced, and the visible light transmittance can be improved. Therefore, the upper limit of the content of the Bi ₂ O ₃ component is preferably 10.0%, more preferably 5.0%, and more preferably 3.0%. As the Bi ₂ O ₃ component, Bi ₂ O ₃ or the like can be used as a raw material.

The TeO ₂ component is any component that can increase the refractive index and lower the glass transition point when the content is greater than 0%. However, there is a problem that the TeO ₂ component may be alloyed with platinum when the glass raw material is placed in a crucible made of platinum or when the part in contact with the molten glass is placed in a melting tank made of platinum. Therefore, the upper limit of the content of the TeO ₂ component is preferably 10.0%, more preferably 5.0%, more preferably 3.0%, and more preferably none. TeO ₂ component, TeO ₂ etc. can be used as raw materials.

The SnO ₂ component is any component that, when the content is greater than 0%, can reduce the oxidation of the molten glass to make the molten glass clear, and is less likely to deteriorate the light transmittance of the glass. On the other hand, by setting the content of the SnO ₂ component to 3.0% or less, glass coloring or glass devitrification due to reduction of molten glass is less likely to occur. In addition, since the SnO ₂ component is less alloyed with the melting equipment (especially noble metals such as Pt), the service life of the melting equipment can be expected to be extended. Therefore, the content of the SnO ₂ component is preferably 3.0% or less, more preferably less than 2.0%, more preferably less than 1.0%, and even more preferably not included. As the SnO ₂ component, SnO, SnO ₂ , SnF ₂ , SnF ₄ , etc. can be used as raw materials.

The Sb ₂ O ₃ component is any component capable of defoaming molten glass when its content is greater than 0%. On the other hand, by setting the content of the Sb ₂ O ₃ component to 1.0% or less, excessive foaming is less likely to occur, and alloying with melting equipment (especially noble metals such as Pt) can be reduced. Therefore, the content of the Sb ₂ O ₃ component is preferably 1.0% or less, more preferably less than 0.5%, more preferably less than 0.3%, still more preferably less than 0.1%. As the Sb ₂ O ₃ component, Sb ₂ O ₃ , Sb ₂ O ₅ , Na ₂ H ₂ Sb ₂ O ₇ ·5H ₂ O, etc. can be used as raw materials.

In addition, the component that clarifies and defoams the glass is not limited to the above-mentioned Sb ₂ O ₃ component, and clarifiers, defoaming agents, or combinations thereof that are well-known in the field of glass manufacturing can be used.

The F component is any component that, when the content is greater than 0%, can increase the Abbe number of the glass, lower the glass transition point, and improve the devitrification resistance. However, if the content of the F component, that is, the total amount of fluoride that replaces part or all of one or more oxides of each metal element, is greater than 10.0%, the volatilization amount of the F component will change. Therefore, it becomes difficult to obtain stable optical constants and homogeneous glass. Furthermore, the Abbe number will rise to a level greater than required. Therefore, the content of the F component is preferably 10.0% or less, preferably less than 5.0%, more preferably less than 3.0%, still more preferably less than 1.0%, still more preferably not included. ＜About ingredients that should not be included＞ Next, components that should not be contained in the optical glass of the present invention and components that are not suitable to be contained will be described.

In the optical glass of the present invention, other components may be added as necessary within the scope that does not affect the properties of the glass of the present invention. However, the GeO ₂ component will increase the dispersion of the glass, so it is better not to contain it substantially.

In addition, various transition metal components other than Ti, Zr, Nb, W, La, Gd, Y, Yb, Lu, such as Hf, V, Cr, Mn, Fe, Co, Ni, Cu, Ag, Mo, Ce, Nd When contained individually or in a composite form, even a small amount will color the glass and absorb light of a specific wavelength in the visible light range. Therefore, it is particularly useful in optical glass using wavelengths in the visible light range. , it is better not to contain it in essence.

In addition, lead compounds such as PbO and arsenic compounds such as As ₂ O ₃ , as well as components such as Th, Cd, Tl, Os, Be, and Se, have been regarded as harmful chemical substances in recent years, and their use has tended to be avoided. Not only In the manufacturing steps of glass, even the processing steps and post-product treatment, environmental countermeasures must be taken. Therefore, when taking the environmental impact into consideration, it is better to substantially not contain these components except for unavoidable mixing. In this way, the optical glass can be substantially free of substances that pollute the environment. Therefore, the optical glass can be manufactured, processed and discarded without taking special environmental countermeasures.

[Manufacturing method] The optical glass of the present invention can be produced in the following manner, for example. That is, the above-mentioned raw materials are uniformly mixed so that each component is within the prescribed content range, and then the prepared mixture is put into a platinum crucible, quartz crucible, or alumina-oxygen crucible for preliminary melting, and then a gold crucible, platinum crucible, and platinum crucible are added. In a crucible, platinum alloy crucible, or iridium crucible, it takes 1 hour to 5 hours to melt in the temperature range of 900°C to 1400°C, stir to homogenize, defoaming, etc., then cool down to below 1300°C, and then It is produced by performing final stirring to remove streaks and then shaping it using a mold. Here, as a method of obtaining glass formed using a forming mold, a method in which molten glass is poured into one end of the forming mold and the formed glass is pulled out from the other end of the forming mold, or a method in which the molten glass is cast in A method of slowly cooling the mold in the mold.

[Physical Properties] The optical glass of the present invention preferably has a high refractive index and high dispersion. In particular, the lower limit of the refractive index (n _d ) of the optical glass of the present invention is preferably 1.90, more preferably 1.95, and more preferably 1.98. The upper limit of the refractive index is preferably 2.20, more preferably less than 2.15, more preferably less than 2.10. In addition, the lower limit of the Abbe number (ν _d ) of the optical glass of the present invention is preferably 15.0, preferably 18.0 or more, and more preferably 20.0 or more, and the upper limit is preferably 30.0 or less, preferably 28.0 or less. Even better is 27.0. By having such a high refractive index, even if it is desired to reduce the thickness of the optical element, a large refractive amount can be obtained. Furthermore, by having such high dispersion, high imaging characteristics can be achieved when, for example, combined with an optical element having low dispersion (high Abbe number). Therefore, the optical glass of the present invention can play an important role in optical design. In particular, in addition to expecting high imaging properties, it can also achieve miniaturization of the optical system, thereby increasing the degree of freedom in optical design.

The optical glass of the present invention preferably has a high transmittance of visible light, especially a high transmittance of light with short wavelengths in visible light, thereby reducing coloring. In particular, if the optical glass of the present invention is expressed in terms of glass transmittance, in a sample with a thickness of 10 mm, the wavelength (λ ₇₀ ) at which the spectral transmittance is 70% is expressed, and the upper limit is preferably 500 nm, preferably 500 nm. 490nm, preferably 480nm. In addition, in the optical glass of the present invention, the shortest wavelength (λ ₅ ) showing a spectral transmittance of 5% in a sample with a thickness of 10 mm has an upper limit of 400 nm, preferably 390 nm. As a result, the absorption edge of the glass becomes near the ultraviolet light region, which can improve the transparency of the glass to visible light. Therefore, the optical glass can be suitable for optical elements that transmit light, such as lenses.

The optical glass of the present invention preferably has a high partial dispersion ratio (θg, F). More specifically, the lower limit of the partial dispersion ratio (θg, F) of the optical glass of the present invention is preferably 0.570, more preferably 0.580, more preferably 0.595, still more preferably 0.605, still more preferably 0.612. In addition, the relationship between the partial dispersion ratio (θg,F) of the optical glass of the present invention and the Abbe number (ν _d ) is preferably in line with (−0.00162ν _d +0.645)≦(θg,F)≦(− 0.00162ν _d +0.680) relationship. Thereby, optical glass with a small partial dispersion ratio (θg, F) can be obtained, and the optical glass can play a role in reducing chromatic aberration of optical elements. Therefore, the lower limit of the partial dispersion ratio (θg, F) of the optical glass of the present invention is preferably (−0.00162ν _d +0.645), and more preferably (−0.00162ν _d +0.650). On the other hand, the upper limit of the partial dispersion ratio (θg, F) of the optical glass of the present invention is preferably (−0.00162ν _d +0.675), and more preferably (−0.00162ν _d +0.670).

The above relationship between the partial dispersion ratio (θg,F) and the Abbe number (ν _d ) is based on a straight line parallel to the normal in a rectangular coordinate system with the partial dispersion ratio as the vertical axis and the Abbe number as the horizontal axis. to express. The normal line represents the linear relationship observed between the partial dispersion ratio (θg, F) and the Abbe number (ν _d ) of conventionally known glasses. Here, the partial dispersion ratio (θg, F) is used as the vertical axis. , the Abbe number (ν _d ) is a rectangular coordinate on the horizontal axis, and is represented by a straight line connecting the two points labeled NSL7 and PBM2, the partial dispersion ratio and the Abbe number (please refer to Figure 1). Furthermore, the relationship between the partial dispersion ratio and the Abbe number of glass that has been known in the past is roughly the same as that of the normal line. Here, NSL7 and PBM2 are optical glasses manufactured by Ohara Corporation. The Abbe number (ν _d ) of PBM2 is 36.3 and the partial dispersion ratio (θg, F) is 0.5828. The Abbe number (ν _d ) of NSL7 is 60.5. The dispersion ratio (θg,F) is 0.5436.

[Preforms and optical components] A glass molded body can be produced from the optical glass produced by, for example, grinding processing, or press molding methods such as reheat press molding and precision press molding. That is, a glass molded body can be produced in the following manner: the optical glass is subjected to mechanical processing such as grinding and grinding to produce a glass molded body; a preform made of optical glass is reheated and pressed into shape, and then polished. Processing to produce a glass molded body; Preformed bodies produced by grinding or preforms molded by well-known float molding, etc., are precision press-molded to produce glass molded bodies, etc. However, the method of producing a glass formed body is not limited to the above.

In this way, the glass molded body formed of the optical glass of the present invention can be used in various optical elements and optical designs, and is particularly suitable for use in optical elements such as lenses and lenses. By improving the stability of the glass, a glass molded body with a large diameter can be formed. Therefore, in addition to the enlargement of optical elements, it is also possible to achieve high definition and high precision when used in optical equipment such as cameras and projectors. imaging characteristics and projection characteristics. [Example]

The glass compositions of the embodiments of the present invention (No. 1 to No. 52), and the refractive index (n _d ), Abbe number (ν _d ), transmittance (λ ₅ , λ ₇₀ ), and partial The values of the dispersion ratio (θg, F) are shown in Table 1 to Table 10. In addition, the following examples are only for illustrative purposes, and the present invention is not limited to these examples.

The raw materials of each component of the glass in the examples are selected from high-purity raw materials used in general optical glass such as oxides, hydroxides, carbonates, nitrates, fluorides, hydroxides, and metaphosphate compounds. , then weigh the raw materials and mix them evenly, put them into a platinum crucible, and use an electric furnace with a temperature set in the range of 1280°C to 1340°C. It takes 2.5 hours to melt the glass raw materials and stir the melted glass. After the raw materials are defoamed, the temperature is lowered to 1180°C to 1250°C, stirred again to homogenize, cast into a mold, and slowly cooled to produce glass.

The refractive index (n _d ) and Abbe's number (ν _d ) of the glass in Examples are expressed as measured values relative to the d line (587.56 nm) of a helium lamp. In addition, the Abbe number (ν _d ) is calculated using the refractive index of the d line mentioned above, the refractive index (n F ) with respect to the F line (486.13 nm) of the hydrogen lamp, and the refractive index (n _F ) with respect to the C line (656.27 nm). The value of n _C ) is calculated from the expression Abbe number (ν _d )=[(n _d −1)/(n _F −n _C )]. The partial dispersion ratio is to measure the refractive index n _C in the C line (wavelength 656.27nm), the refractive index n _F in the F line (wavelength 486.13nm), and the refractive index n _g in the g line (wavelength 435.835nm), and then borrow This part of the dispersion ratio is calculated from the formula (θg,F)=(n _g −n _F )/(n _F −n _C ).

The transmittance of the glass of the Example was measured based on the Japan Optical Glass Industry Association standard JOGIS02-2003. In addition, in the present invention, the presence or absence of coloring of the glass and the degree of coloring are determined by measuring the transmittance of the glass. Specifically, the spectral transmittance from 200 nm to 800 nm is measured according to JISZ8722 on relatively parallel abrasive articles with a thickness of 10±0.1 mm, and λ ₅ (wavelength at which the transmittance is 5%) and λ ₇₀ are obtained. (Wavelength when transmittance is 70%). In addition, the glass used in this measurement was processed in a slow cooling furnace with a slow cooling rate of −25°C/hr.

[Table 1] wt% 1 2 3 4 5 6 SiO ₂ 6.01 6.01 6.01 5.43 5.01 5.01 B ₂ O ₃ 6.95 6.95 6.95 7.60 6.95 6.95 La ₂ O ₃ 31.99 32.00 33.27 31.72 32.00 33.98 Y ₂ O ₃ Gd ₂ O ₃ Yb ₂ O ₃ ZrO ₂ 6.39 6.39 6.39 6.37 6.39 4.39 TiO ₂ 21.70 21.70 21.70 21.89 22.70 21.70 Nb ₂ O ₅ 7.31 7.31 7.31 8.78 7.31 8.31 WO ₃ 0.77 0.77 0.77 0.77 0.77 0.77 ZnO 1.27 1.27 1.27 1.27 Li ₂ O Na ₂ O K ₂ O MgO CaO sO BO 17.60 17.60 17.60 17.45 17.60 17.60 Sb ₂ O ₃ 0.01 0.00 0.00 0.00 0.00 0.02 total 100.00 100.00 100.00 100.00 100.00 100.00 Si+B 12.96 12.96 12.96 13.03 11.96 11.96 Ti/(Ti+Ba) 0.55 0.55 0.55 0.56 0.56 0.55 La+Nb+Gd+Yb 39.30 39.31 40.58 40.50 39.31 42.29 Ti/Ba 1.23 1.23 1.23 1.25 1.29 1.23 Rn ₂ O 0.00 0.00 0.00 0.00 0.00 0.00 RO 17.60 17.60 17.60 17.45 17.60 17.60 Ln 31.99 32.00 33.27 31.72 32.00 33.98 Ti+Nb 29.01 29.01 29.01 30.66 30.01 30.01 (Ti+W)/Ba 1.28 1.28 1.28 1.30 1.33 1.28 La/(Nb+Gd+Yb) 4.38 4.38 4.55 3.62 4.38 4.09 n _d 2.012 2.012 2.012 2.018 2.025 2.020 ν _d 24.9 24.9 25.0 24.5 24.4 24.7 θ g,F 0.6156 0.6155 0.6138 0.6168 0.6167 0.6150 λ ₇₀ 447 448 447 459 451 454 λ ₅ 373 372 372 375 373 374

[Table 2] wt% 7 8 9 10 11 12 SiO ₂ 5.01 5.51 5.51 5.51 5.51 5.51 B ₂ O ₃ 6.95 7.45 7.45 7.45 7.45 7.45 La ₂ O ₃ 32.48 29.48 30.08 30.08 30.08 29.58 Y ₂ O ₃ Gd ₂ O ₃ Yb ₂ O ₃ ZrO ₂ 5.89 5.89 5.89 5.89 5.89 5.79 TiO ₂ 21.70 21.70 21.70 21.70 21.70 21.70 Nb ₂ O ₅ 8.31 10.31 10.31 10.61 10.61 10.31 WO ₃ 0.77 0.77 0.77 0.77 0.77 0.77 ZnO 1.27 1.27 0.67 0.67 3.67 1.27 Li ₂ O Na ₂ O K ₂ O MgO CaO sO BO 17.60 17.60 17.60 17.30 14.30 17.60 Sb ₂ O ₃ 0.02 0.02 0.02 0.02 0.02 0.02 total 100.00 100.00 100.00 100.00 100.00 100.00 Si+B 11.96 12.96 12.96 12.96 12.96 12.96 Ti/(Ti+Ba) 0.55 0.55 0.55 0.56 0.60 0.55 La+Nb+Gd+Yb 40.79 39.79 40.39 40.69 40.69 39.89 Ti/Ba 1.23 1.23 1.23 1.25 1.52 1.23 Rn ₂ O 0.00 0.00 0.00 0.00 0.00 0.00 RO 17.60 17.60 17.60 17.30 14.30 17.60 Ln 32.48 29.48 30.08 30.08 30.08 29.58 Ti+Nb 30.01 32.01 32.01 32.31 32.31 32.01 (Ti+W)/Ba 1.28 1.28 1.28 1.30 1.57 1.28 La/(Nb+Gd+Yb) 3.91 2.86 2.92 2.84 2.84 2.87 n _d 2.022 2.021 2.021 2.023 2.027 2.020 ν _d 24.6 24.2 24.2 24.1 24.0 24.2 θ g,F 0.6157 λ ₇₀ 468 459 457.5 463 462 467 λ ₅ 376 377 377 377.5 378 378

[table 3] wt% 13 14 15 SiO ₂ 5.51 5.51 5.51 B ₂ O ₃ 7.45 7.45 7.45 La ₂ O ₃ 31.48 29.48 33.48 Y ₂ O ₃ Gd ₂ O ₃ Yb ₂ O ₃ ZrO ₂ 5.89 5.89 5.89 TiO ₂ 21.70 21.70 21.70 Nb ₂ O ₅ 10.31 10.31 10.31 WO ₃ 0.77 0.77 0.77 ZnO 1.27 1.27 1.27 Li ₂ O Na ₂ O K ₂ O MgO CaO sO BO 15.60 17.60 13.60 Sb ₂ O ₃ 0.02 0.02 0.02 total 100.00 100.00 100.00 Si+B 12.96 12.96 12.96 Ti/(Ti+Ba) 0.58 0.55 0.61 La+Nb+Gd+Yb 41.79 39.79 43.79 Ti/Ba 1.39 1.23 1.60 Rn ₂ O 0.00 0.00 0.00 RO 15.60 17.60 13.60 Ln 31.48 29.48 33.48 Ti+Nb 32.01 32.01 32.01 (Ti+W)/Ba 1.44 1.28 1.65 La/(Nb+Gd+Yb) 3.05 2.86 3.25 n _d 2.026 2.021 2.031 ν _d 24.2 24.2 24.2 θ g,F λ ₇₀ 467 467 470 λ ₅ 379 378 380

[Table 4] wt% 16 17 18 19 20 twenty one SiO ₂ 6.01 6.01 6.01 6.01 6.01 6.01 B ₂ O ₃ 7.70 7.70 7.70 7.70 7.70 7.70 La ₂ O ₃ 33.03 33.03 33.03 32.53 33.53 33.03 Y ₂ O ₃ Gd ₂ O ₃ Yb ₂ O ₃ ZrO ₂ 6.39 6.39 6.39 6.89 5.89 6.39 TiO ₂ 20.90 20.90 20.90 20.90 20.90 20.90 Nb ₂ O ₅ 6.91 7.31 6.71 6.71 6.71 6.91 WO ₃ 0.77 0.77 0.77 0.77 0.77 0.77 ZnO 1.27 1.27 1.27 1.27 1.27 1.27 Li ₂ O Na ₂ O K ₂ O MgO CaO sO BO 17.00 16.60 17.20 17.20 17.20 17.00 Sb ₂ O ₃ 0.02 0.02 0.02 0.02 0.02 0.02 total 100.00 100.00 100.00 100.00 100.00 100.00 Si+B 13.71 13.71 13.71 13.71 13.71 13.71 Ti/(Ti+Ba) 0.55 0.56 0.55 0.55 0.55 0.55 La+Nb+Gd+Yb 39.94 40.34 39.74 39.24 40.24 39.94 Ti/Ba 1.23 1.26 1.22 1.22 1.22 1.23 Rn ₂ O 0.00 0.00 0.00 0.00 0.00 0.00 RO 17.00 16.60 17.20 17.20 17.20 17.00 Ln 33.03 33.03 33.03 32.53 33.53 33.03 Ti+Nb 27.81 28.21 27.61 27.61 27.61 27.81 (Ti+W)/Ba 1.27 1.31 1.26 1.26 1.26 1.27 La/(Nb+Gd+Yb) 4.78 4.52 4.92 4.85 5.00 4.78 n _d 2.001 2.003 2.000 2.001 1.999 2.001 ν _d 25.4 25.3 25.5 25.4 25.5 25.4 θ g,F 0.6141 0.6137 0.6133 0.6132 0.6133 0.6136 λ ₇₀ 446 450 458 451 450 449 λ ₅ 373 374 374 373 373 373

[table 5] wt% twenty two twenty three twenty four 25 26 27 SiO ₂ 6.01 6.01 6.01 6.01 6.01 6.01 B ₂ O ₃ 7.70 7.70 7.70 7.70 7.70 7.70 La ₂ O ₃ 33.03 33.03 33.03 33.03 33.03 38.03 Y ₂ O ₃ Gd ₂ O ₃ Yb ₂ O ₃ ZrO ₂ 6.39 6.39 6.39 6.39 6.39 6.39 TiO ₂ 20.90 20.90 20.90 20.90 20.90 20.90 Nb ₂ O ₅ 6.91 6.91 6.91 6.91 6.91 6.91 WO ₃ 0.77 0.77 0.77 0.77 0.77 0.77 ZnO 6.27 0.77 2.27 4.27 1.27 Li ₂ O Na ₂ O K ₂ O MgO CaO sO BO 18.27 12.00 17.50 16.00 14.00 12.00 Sb ₂ O ₃ 0.02 0.02 0.02 0.02 0.02 0.02 total 100.00 100.00 100.00 100.00 100.00 100.00 Si+B 13.71 13.71 13.71 13.71 13.71 13.71 Ti/(Ti+Ba) 0.53 0.64 0.54 0.57 0.60 0.64 La+Nb+Gd+Yb 39.94 39.94 39.94 39.94 39.94 44.94 Ti/Ba 1.14 1.74 1.19 1.31 1.49 1.74 Rn ₂ O 0.00 0.00 0.00 0.00 0.00 0.00 RO 18.27 12.00 17.50 16.00 14.00 12.00 Ln 33.03 33.03 33.03 33.03 33.03 38.03 Ti+Nb 27.81 27.81 27.81 27.81 27.81 27.81 (Ti+W)/Ba 1.19 1.81 1.24 1.35 1.55 1.81 La/(Nb+Gd+Yb) 4.78 4.78 4.78 4.78 4.78 5.50 n _d 1.998 2.009 2.000 2.003 2.006 2.014 ν _d 25.5 25.2 25.5 25.4 25.3 25.4 θ g,F 0.6133 0.6153 0.6132 0.6138 0.6136 0.6130 λ ₇₀ 462 459 451 459 453 454 λ ₅ 375 375 373 375 374 375

[Table 6] wt% 28 29 30 31 32 33 SiO ₂ 6.01 6.01 6.01 6.01 6.01 6.01 B ₂ O ₃ 7.70 7.70 7.70 7.70 7.70 7.70 La ₂ O ₃ 34.03 36.03 34.83 34.83 34.83 34.83 Y ₂ O ₃ Gd ₂ O ₃ Yb ₂ O ₃ ZrO ₂ 6.39 6.39 6.39 6.39 6.39 6.39 TiO ₂ 20.90 20.90 20.10 20.10 20.10 20.10 Nb ₂ O ₅ 6.91 6.91 6.91 5.91 6.91 5.91 WO ₃ 0.77 0.77 0.77 1.77 0.77 1.77 ZnO 1.27 1.27 1.27 1.27 1.27 1.27 Li ₂ O Na ₂ O K ₂ O MgO CaO sO BO 16.00 14.00 16.00 16.00 16.00 16.00 Sb ₂ O ₃ 0.02 0.02 0.02 0.02 0.02 0.02 total 100.00 100.00 100.00 100.00 100.00 100.00 Si+B 13.71 13.71 13.71 13.71 13.71 13.71 Ti/(Ti+Ba) 0.57 0.60 0.56 0.56 0.56 0.56 La+Nb+Gd+Yb 40.94 42.94 41.74 40.74 41.74 40.74 Ti/Ba 1.31 1.49 1.26 1.26 1.26 1.26 Rn ₂ O 0.00 0.00 0.00 0.00 0.00 0.00 RO 16.00 14.00 16.00 16.00 16.00 16.00 Ln 34.03 36.03 34.83 34.83 34.83 34.83 Ti+Nb 27.81 27.81 27.01 26.01 27.01 26.01 (Ti+W)/Ba 1.35 1.55 1.30 1.37 1.30 1.37 La/(Nb+Gd+Yb) 4.92 5.21 5.04 5.89 5.04 5.89 n _d 2.003 2.008 1.999 1.999 1.999 1.999 ν _d 25.4 25.4 25.8 25.8 25.8 25.8 θ g,F 0.6137 0.6137 0.6124 0.6124 0.6119 0.6118 λ ₇₀ 453 451 442 445 λ ₅ 374 374 372 372

[Table 7] wt% 34 35 36 37 38 39 SiO ₂ 6.01 6.01 6.01 6.01 6.01 6.01 B ₂ O ₃ 7.70 7.70 7.70 7.70 7.70 7.70 La ₂ O ₃ 34.84 34.84 34.84 34.14 33.64 34.64 Y ₂ O ₃ Gd ₂ O ₃ Yb ₂ O ₃ ZrO ₂ 6.39 6.39 6.39 6.39 6.89 5.89 TiO ₂ 20.10 20.10 20.10 20.80 20.80 20.80 Nb ₂ O ₅ 6.91 6.91 6.91 6.91 6.91 6.91 WO ₃ 0.77 0.77 0.77 0.77 0.77 0.77 ZnO 1.27 1.27 1.27 1.27 1.27 1.27 Li ₂ O Na ₂ O K ₂ O MgO CaO sO BO 16.00 16.00 16.00 16.00 16.00 16.00 Sb ₂ O ₃ 0.01 0.01 0.01 0.01 0.01 0.01 total 100.00 100.00 100.00 100.00 100.00 100.00 Si+B 13.71 13.71 13.71 13.71 13.71 13.71 Ti/(Ti+Ba) 0.56 0.56 0.56 0.57 0.57 0.57 La+Nb+Gd+Yb 41.75 41.75 41.75 41.05 40.55 41.55 Ti/Ba 1.26 1.26 1.26 1.30 1.30 1.30 Rn ₂ O 0.00 0.00 0.00 0.00 0.00 0.00 RO 16.00 16.00 16.00 16.00 16.00 16.00 Ln 34.84 34.84 34.84 34.14 33.64 34.64 Ti+Nb 27.01 27.01 27.01 27.71 27.71 27.71 (Ti+W)/Ba 1.30 1.30 1.30 1.35 1.35 1.35 La/(Nb+Gd+Yb) 5.04 5.04 5.04 4.94 4.87 5.01 n _d 1.999 1.999 1.999 2.003 2.003 2.002 ν _d 25.8 25.8 25.8 25.5 25.4 25.5 θ g,F 0.6116 0.6116 0.6119 0.6139 0.6137 0.6131 λ ₇₀ 444.5 454 448.5 λ ₅ 371.5 373 372

[Table 8] wt% 40 41 42 43 44 45 SiO ₂ 6.21 6.01 6.01 6.01 6.01 6.01 B ₂ O ₃ 7.85 8.02 7.70 8.02 8.02 8.02 La ₂ O ₃ 33.33 33.82 34.34 33.83 33.83 33.83 Y ₂ O ₃ Gd ₂ O ₃ Yb ₂ O ₃ ZrO ₂ 6.39 6.39 6.19 6.39 6.39 6.39 TiO ₂ 20.90 21.10 20.80 21.10 21.10 21.10 Nb ₂ O ₅ 6.91 6.61 6.91 6.61 6.61 6.61 WO ₃ 0.77 0.77 0.77 0.77 0.77 0.77 ZnO 1.27 1.27 1.27 1.27 1.27 1.27 Li ₂ O Na ₂ O K ₂ O MgO CaO sO BO 16.35 16.00 16.00 16.00 16.00 16.00 Sb ₂ O ₃ 0.02 0.01 0.01 0.00 0.00 0.00 total 100.00 100.00 100.00 100.00 100.00 100.00 Si+B 14.06 14.03 13.71 14.03 14.03 14.03 Ti/(Ti+Ba) 0.56 0.57 0.57 0.57 0.57 0.57 La+Nb+Gd+Yb 40.24 40.43 41.25 40.44 40.44 40.44 Ti/Ba 1.28 1.32 1.30 1.32 1.32 1.32 Rn ₂ O 0.00 0.00 0.00 0.00 0.00 0.00 RO 16.35 16.00 16.00 16.00 16.00 16.00 Ln 33.33 33.82 34.34 33.83 33.83 33.83 Ti+Nb 27.81 27.71 27.71 27.71 27.71 27.71 (Ti+W)/Ba 1.33 1.37 1.35 1.37 1.37 1.37 La/(Nb+Gd+Yb) 4.82 5.12 4.97 5.12 5.12 5.12 n _d 1.999 2.001 2.002 2.000 2.001 2.001 ν _d 25.5 25.4 25.5 25.4 25.4 25.4 θ g,F 0.6138 0.6131 0.6128 0.6135 0.6126 0.6132 λ ₇₀ 460 447 447 450 452 λ ₅ 375 372 372 372 373

[Table 9] wt% 46 47 48 49 50 51 SiO ₂ 6.21 6.12 6.63 7.87 6.55 8.14 B ₂ O ₃ 7.85 8.02 10.10 10.02 9.98 10.43 La ₂ O ₃ 33.41 33.73 41.27 37.39 31.49 36.13 Y ₂ O ₃ Gd ₂ O ₃ Yb ₂ O ₃ ZrO ₂ 6.39 6.39 6.37 6.68 5.51 6.85 TiO ₂ 20.83 21.08 16.68 18.48 14.30 16.76 Nb ₂ O ₅ 6.91 6.61 6.34 5.56 13.88 2.39 WO ₃ 0.77 0.77 0.82 5.19 2.48 ZnO 1.27 1.27 1.36 1.61 1.34 2.20 Li ₂ O Na ₂ O K ₂ O MgO CaO sO BO 16.35 16.00 10.43 12.38 11.75 14.61 Sb ₂ O ₃ 0.01 0.01 0.01 0.01 0.01 0.01 total 99.99 100.00 100.00 100.00 100.00 100.00 Si+B 14.06 14.14 16.73 17.89 16.53 18.57 Ti/(Ti+Ba) 0.56 0.57 0.62 0.60 0.55 0.53 La+Nb+Gd+Yb 40.32 40.34 47.61 42.96 45.36 38.52 Ti/Ba 1.27 1.32 1.60 1.49 1.22 1.15 Rn ₂ O 0.00 0.00 0.00 0.00 0.00 0.00 RO 16.35 16.00 10.43 12.38 11.75 14.61 Ln 33.41 33.73 41.27 37.39 31.49 36.13 Ti+Nb 27.74 27.69 23.02 24.04 28.18 19.15 (Ti+W)/Ba 1.32 1.37 1.68 1.49 1.66 1.32 La/(Nb+Gd+Yb) 4.83 5.10 6.51 6.72 2.27 15.10 n _d 1.999 2.000 1.968 1.961 1.976 1.934 ν _d 25.5 25.5 27.8 27.4 26.1 28.8 θ g,F 0.6131 0.6134 0.6053 0.6081 0.6115 0.6040 λ ₇₀ 455 444 440 428 436 420 λ ₅ 375 372 369 369 373 367

[Table 10] wt% 52 SiO ₂ 6.21 B ₂ O ₃ 7.85 La ₂ O ₃ 33.41 Y ₂ O ₃ Gd ₂ O ₃ ybO3 ZrO ₂ 6.39 TiO ₂ 20.83 Nb ₂ O ₅ 6.91 WO ₃ 0.77 ZnO 1.27 Li ₂ O 0.10 Na ₂ O K ₂ O MgO CaO sO BO 16.35 Sb ₂ O ₃ total 100.08 Si+B 14.06 Ti/(Ti+Ba) 0.56 La+Nb+Gd+Yb 40.32 Ti/Ba 1.27 Rn ₂ O 0.10 RO 16.35 Ln 33.41 Ti+Nb 27.74 (Ti+W)/Ba 1.32 La/(Nb+Gd+Yb) 4.83 n _d 1.999 ν _d 25.5 θ g,F 0.6130 λ ₇₀ 449 λ ₅ 372

As shown in the table, the refractive index (n _d ) of the optical glass according to the embodiment of the present invention is 1.90 or more, and the refractive index (n _d ) is also 2.20 or less, and more specifically, it is 2.10 or less. All within the expected range. In addition, the Abbe number (ν _d ) of the optical glass according to the embodiment of the present invention is 30.0 or less, more specifically, 28.0 or less, and the Abbe number (ν d ) is also 15.0 or more, and more specifically, the Abbe number (ν _d ) is 15.0 or more. Specifically, it is above 20.0, which is within the expected range.

In addition, in the optical glass according to the embodiments of the present invention, λ ₇₀ (the wavelength when the transmittance is 70%) is all 500 nm or less, and more specifically, 490 nm or less. In addition, in the optical glass according to the embodiments of the present invention, λ ₅ (wavelength when the transmittance is 5%) is all 400 nm or less, and more specifically, 390 nm or less.

In addition, regardless of the optical glass according to the embodiment of the present invention, the partial dispersion ratio (θg, F) is (−0.00162ν _d +0.645) or more, and more specifically, it is (−0.00162ν _d +0.650) or more. On the contrary, the partial dispersion ratio of the optical glass according to the embodiment of the present invention is (−0.00162ν _d +0.680) or less, and more specifically, it is (−0.00162ν _d +0.670) or less. Therefore, it can be seen that the partial dispersion ratios (θg, F) are within the desired range.

Therefore, it is clear that the optical glass according to the embodiment of the present invention can not only have the refractive index and Abbe number within the desired range, but can also be produced at low cost and can reduce coloration.

Furthermore, the optical glass obtained according to the embodiment of the present invention was reheated and pressed into shape, and then grinded and polished to be processed into the shapes of lenses and lenses. Furthermore, the optical glass according to the embodiment of the present invention was used to form a preform for precision press molding, and then the preform for precision press molding was precision press-formed. Regardless of the situation, glass softened by heating will not cause problems such as opalescence and devitrification, and can be stably processed into a variety of lens and lens shapes.

Although the present invention has been described in detail for the purpose of illustration, the purpose of this embodiment is only illustrative. It should be understood by those with ordinary skill in the technical field that without departing from the spirit and scope of the present invention, The invention is still susceptible to many variations.

[Fig. 1] is a schematic diagram showing the normal line represented by rectangular coordinates with the partial dispersion ratio (θg, F) as the vertical axis and the Abbe number (ν _d ) as the horizontal axis. [Fig. 2] is a schematic diagram showing the relationship between the partial dispersion ratio (θg, F) and the Abbe number (ν _d ) of the glass according to the embodiment of the present invention.

Claims (12)

An optical glass containing, in mass % on an oxide basis,: a La ₂ O ₃ composition of greater than 0% to 45.0%; a TiO ₂ composition of greater than 20% to 45.0%; and a BaO composition of greater than 0% to 40.0%; and containing SiO The total amount of the ₂ component and the B ₂ O ₃ component is 5.0% or more and 12.96% or less; the mass ratio of TiO ₂ /(TiO ₂ +BaO) is 0.10 or more and 0.90 or less; the refractive index (n _d ) is 1.98 or more, A The Bay number (ν _d ) is 27.0 or less, and the wavelength (λ ₅ ) indicating 5% spectral transmittance is 400 nm or less. The optical glass according to claim 1, wherein the SiO ₂ component is 0% to 11.0% in mass % on an oxide basis; and the B ₂ O ₃ component is 0% to 12.0%. The optical glass as described in claim 1 or 2, wherein the ZnO component is 0% to 20.0%; the Y ₂ O ₃ component is 0% to 15.0%; and the Nb ₂ O ₅ component is 0% in terms of mass % on an oxide basis. to 25.0%; Yb ₂ O ₃ composition is 0% to 15.0%; and Gd ₂ O ₃ composition is 0% to 15.0%. Optical glass as described in claim 1 or 2, wherein the mass sum of (La ₂ O ₃ +Nb ₂ O ₅ +Gd ₂ O ₃ +Yb ₂ O ₃ ) is greater than 0% in terms of mass % on an oxide basis to below 60.0%. The optical glass according to claim 1 or 2, wherein the Ln ₂ O ₃ component (in the formula, Ln is one selected from the group consisting of La, Gd, Y, and Yb) is calculated as oxide-based mass %. The total amount of the above) is greater than 0% and less than 50.0%. The optical glass according to claim 1 or 2, wherein the mass ratio of TiO ₂ /BaO is 0.60 or more and 3.00 or less on an oxide basis. The optical glass according to claim 1 or 2, wherein the Rn ₂ O component (in the formula, Rn is one or more species selected from the group consisting of Li, Na, and K) is calculated as mass % on an oxide basis. The mass sum is 15.0% or less. The optical glass according to claim 1 or 2, wherein the RO component (in the formula, R is one or more species selected from the group consisting of Mg, Ca, Sr, and Ba) is calculated as mass % on an oxide basis. The mass sum is greater than 0% and less than 35.0%. Optical glass as described in claim 1 or 2, which contains, in mass % based on oxides: ZrO ₂ component 0% to 20.0%; WO ₃ component 0% to 10.0%; Ta ₂ O ₅ component 0% to 10.0%; MgO composition 0% to 15.0%; CaO composition 0% to 15.0%; SrO composition 0% to 15.0%; Li ₂ O composition 0% to 15.0%; Na ₂ O composition 0% to 15.0%; K ₂ O component 0% to 15.0%; P ₂ O ₅ component 0% to 10.0%; GeO ₂ component 0% to 10.0%; Al ₂ O ₃ component 0% to 15.0%; Ga ₂ O ₃ component 0% to 15.0%; Bi ₂ O ₃ composition 0% to 10.0%; TeO ₂ composition 0% to 10.0%; SnO ₂ composition 0% to 3.0%; and Sb ₂ O ₃ composition 0% to 1.0%. A preform made of the optical glass described in any one of claims 1 to 9. An optical element made of the optical glass described in any one of claims 1 to 9. An optical machine provided with the optical element described in claim 11.