TW201245078A - Optical glass, preform, and optical element - Google Patents

Abstract

Provided is an optical glass exhibiting enhanced transparency with regard to visible light and having a small Abbe number (?d) and partial dispersion ratio (?g,F) while the refraction index (nd) is within a desired range. The optical glass contains, relative to the entire amount of the glass in terms of oxides, 20.0% to 60.0% of an SiO2 component and more than 20.0% to 50.0% or less of a CaO component, a total of more than 0% and 20.0% or less of a BaO component and a K2O component, and has an Nb2O5 component content of 30.0% or less, wherein the partial dispersion ratio (?g,F) and the Abbe number (?d) satisfy the relationship of (-0.00162?d+0.63822)=(?g,F)=(-0.00275?d+0.68125) when ?d=31 and satisfy the relationship of (-0.00162?d+0.63822)=(?g,F)=(-0.00162?d+0.64622) when ?d>31.

Description

201245078 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] An optical system such as a digital camera or a video camera includes blurs of a size, called aberration. The aberration is classified into monochromatic aberration and chromatic aberration, and in particular, the chromatic aberration strongly depends on the material properties of the lens used in the optical system. Generally, the chromatic aberration is combined with a low-dispersion convex lens and a highly-dispersed concave lens. However, in this combination, only the aberration of the red region and the green region can be corrected, and the aberration of the blue region remains. The aberration of the blue region which cannot be completely removed is referred to as a secondary spectrum. In order to correct the secondary spectrum, an optical design in consideration of the direction of the g-line (435.835 nm) of the blue region is required. At this time, as an index of the optical characteristics of the optical design, a partial dispersion ratio (0g, F) was used. In the above optical system combining a low-dispersion lens and a highly-dispersed lens, an optical material having a large partial dispersion ratio (0g, F) is used in a lens on a low dispersion side, and a partial dispersion ratio is used in a lens on a high dispersion side. (eg, F) a smaller optical material whereby the secondary spectrum is well corrected. The partial dispersion ratio (eg, f) is represented by the following formula. 0g, F=(ng-nF)/(nF-nc) (1) For optical glass, the partial dispersion ratio (eg, f) and Abbe number (Vd) indicating partial dispersion in the short wavelength region Between the two, there is a general linear relationship indicating that the relationship is based on the vertical axis using the partial dispersion ratio f), and the horizontal axis using the Abbe number (vd) on the orthogonal coordinates to connect and depict 163467.doc 201245078 The partial dispersion ratio of PBM2 and the straight line of 2 points of the Abbe number are expressed as regular lines (refer to Fig. 1). The standard glass that becomes the basis for the regular line varies according to each optical glass manufacturer, but each company has the same slope and intercept. (NSL7 and PBM2 are optical glass manufactured by OHARA Co., Ltd., the Abbe number (vd) of PBM2 is 36.3, and the partial dispersion ratio (0g, F) is 0.5828'. The Abbe number (vd) of NSL7 is 60.5, partially dispersed. The ratio (0g, ρ) is 0.5436). Here, as the glass having high dispersion, for example, optical glasses as disclosed in Patent Documents 1 to 3 are known. [Patent Document 1] [Patent Document 1] Japanese Patent Laid-Open No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. 2006-219365 (Patent Document 3) [Problem to be Solved by the Invention] However, the partial dispersion ratio of the glass disclosed in Patent Documents 1 to 3 is not small 'not sufficient for the lens used for correcting the above secondary spectrum. . Further, in the glasses disclosed in Patent Documents 1 to 3, the transparency with respect to visible light is not high, and in particular, it is not sufficient for use for transmitting visible light. That is, an optical glass having a small Abbe number (vd) and a high dispersion, a small partial dispersion ratio (eg, F), and a high transparency with respect to visible light is sought. The present invention has been made in view of the above problems, and its object is to obtain a refractive index (nd) which is within a desired range and a small Abbe number (vd) 'part -4 · 163467.doc

201245078 Optical glass having a small dispersion ratio (9g, F) and improved transparency with respect to visible light, and a preform and an optical element using the optical glass ❶ [Technical means for solving the problem] The present inventors have solved the above The subject was repeatedly subjected to intensive experimental research, and as a result, it was found that by using the Si〇2 component and the Ca〇 component in combination and setting the content within a specific range, stable glass can be formed, and the Abbe number can be realized (vd). ), and the color of the glass is reduced. Further, it has been found that a desired high refractive index can be obtained by using a BaO component or more of the BaO component and the κ:2〇 component, and a lower partial dispersion ratio (〇g' F) can be obtained. Further, it has been found that by setting the content of the Nth component within a specific range, a lower Abbe number and a partial dispersion ratio can be obtained, and the devitrification of the glass is alleviated, and the present invention is finally completed. At the same time, it has been found that by using the Si 2 component and the CaO component in combination, and setting the contents in a specific range, coloring or devitrification is less likely to occur when the glass is reheated. Also, 'it is found that by setting the content of Nb>2〇5 component within a specific range', a higher refractive index or a lower Abbe number, a lower partial dispersion ratio, and glass devitrification can be obtained. Reduced. Specifically, the present invention provides the following. (1) An optical glass which is based on the total mass of the glass of the oxide-converted composition, in terms of % by mole, contains 20.0% or more and 60.0% or less of the Si 〇 2 component, and has a CaO component of more than 2 〇. 〇 0 / 0 and 50·0ο/〇, the content of the Nb2〇5 component is 30.0% or less, and is satisfied between the partial dispersion ratio (0g, F) and the Abbe number (vd) in the range of vd$3 1 (_〇 〇〇i62xvcl+〇.63822)S(0g,F)S (-0.00275xvd+0.68125) The relationship 'in the range of Vd>31 satisfies 163467.doc 201245078 (-〇.〇〇162xvd+〇.63822)^(0g , F)^(-0.00162xvd+0.64622)^ Relationship. (2) The optical glass of (1), wherein the sum of the contents of the BaO component and the κ:2〇 component is more than 〇% and 20.0% or less with respect to the total mass of the glass of the oxide-converted composition. (3) The optical glass of (1) or (2), wherein the total mass of the glass in terms of oxide conversion is 〇% to 2% by weight based on the mole % of the TiO2 component. (4) The optical glass according to any one of (1) to (3), wherein the total mass of the glass relative to the oxide-converted composition is from 0% to 10.0% in terms of mol%. (5) The optical glass according to any one of (1) to (4), wherein the sum of the contents of the Nb2〇5 component and the Ti〇2 component is 10·0 with respect to the total mass of the glass of the oxide conversion composition. % or more is 40.0% or less. (6) The optical glass according to any one of (1) to (5), wherein the total mass of the glass relative to the composition of the oxide is from 0 to 25.0% in terms of mol%. (7) The optical glass according to any one of (1) to (6), wherein the mass of the glass relative to the composition of the oxide is in the form of a molar. /. The optical glass containing any one of the items (1) to (7), wherein the oxide ratio is composed of a molar ratio (Nb2〇5+BaO)/ (Ti02 + CaO) is above O.loo. (9) The optical glass according to any one of (1) to (8), wherein the oxide conversion composition has a molar ratio of Ti02/Nb205 of 5.00 or less. (10) The optical glass according to any one of (1) to (9), wherein the oxide is replaced by 163467.doc 201245078 and the molar ratio is Ti〇2/Nb2〇5*3 〇〇 or less. (11) The optical glass according to any one of (1) to (10), wherein the total mass of the glass relative to the oxide-converted composition is in mol%,

Li2〇 component 0~25.0% and/or Na20 component 〇~25.0% and/or K20 component 〇~25.0% and/or Cs20 component 〇~1〇.〇〇/(). (12) The optical glass according to any one of (1) to (11), wherein the RhO component (in the formula, selected from Li, Na, K, Cs) The molar ratio of one or more of the constituent groups is 30.0% or less. (13) The optical glass according to any one of (1) to (12), wherein the total mass of the glass relative to the oxide-converted composition is in mol%,

MgO composition 〇~20.0% and/or SrO composition 〇~20.0% and/or 211〇 composition 〇~3〇.〇〇/. . The optical glass according to any one of (1) to (13), wherein the RO component (wherein, 〒' is selected from the group consisting of Mg, Ca, The molar amount of the group consisting of Sr, Ba, and Zn is 20.0% or more and 60.0% or less. (15) The optical glass according to any one of (1) to (14), wherein the mass of the glass relative to the composition of the oxide is in terms of mol%, ?2〇5 component 0 to 30.0% and/or Or Β2〇3 ingredients 0~40.0% and/or 163467.doc 201245078

Ge〇2 component 〇~2〇〇% and/or Y2O3 component 0~15.0% and/or La203 component 〇~15 〇% and/or Gd203 component 〇1515%% and/or Yb203 component 〇1515%% / or Ta205 ingredient 〇 15 15% and / or 2 〇 3 components 0 ~ 15.0% and / or W03 composition 〇 ~ 2 〇. 0% and / or Te02 composition 〇 ~ 3 〇 0% and / or Zr02 composition 〇 ~15 〇% and/or Al2〇3 components 0~15.0% and/or Sb203 components 〇~1 〇%. (16) The optical glass according to any one of (1) to (15) which has a refractive index (nd) of 17 Å or more and 2.20 or less and an Abbe number (vd) of 20 or more and 40 or less. The optical glass of any one of (1) to (16), wherein the spectral transmittance shows 7 Å. /. The wavelength is 7. ) is 5 〇 () 11 〇 1 or less. (18) The optical glass according to any one of (1) to (17), wherein a transmittance of a light having a wavelength of 587.56 nm (d line) of the test piece after the reheating test (1) is divided by the above The value obtained by the transmittance of the d-line of the test piece before the reheating test was 0.95 or more, [reheating test (2): reheating test piece 15 mm×l5 _ 'from t 'temperature start Μ 15 15 15 minutes to warm up to each test The transfer temperature (Tg) is as high as 80. . The temperature 'is kept at the temperature of 80 ° C higher than the glass transition temperature of 163467.doc 201245078 (Tg) of the optical glass for 30 minutes, and then naturally cooled to normal temperature, and the opposite sides of the test piece are ground to a thickness. After 10 mm, visual observation]. (19) The optical glass according to any one of (1) to (18), wherein the transmittance of the test piece before the reheating test (II) becomes 70% of the wavelength, that is, λ70 and the test after the above reheating test The difference between the λ7〇 of the sheet is 20 nm or less, [reheating test (2): reheating the test piece 15 mm>< 15 mm x 30 mm, and heating from room temperature for 150 minutes to the transfer temperature (Tg) of each sample The temperature of 80 ° C is maintained at a temperature higher than the glass transition temperature (Tg) of the optical glass by 80 ° C for 30 minutes, and then naturally cooled to room temperature until the opposite sides of the test piece are ground to a thickness. After 1 〇mm, visual observation]. (20) A preform for polishing processing and/or precision extrusion molding, which comprises the optical glass according to any one of (1) to (19). (21) An optical element which is obtained by grinding and/or grinding the optical glass of any one of (1) to (19). (22) An optical element which is formed by precisely extruding an optical glass of any one of (19) to (19). [Effects of the Invention] According to the present invention, one or more of the Ba〇 component and the K:2〇 component are used in combination with the Si〇2 component and the CaO component, and the content thereof is set within a specific range. The high refractive index and high dispersion of the glass are achieved, and the desired relationship between the partial dispersion ratio (eg, F) and the Abbe number (vd) of the glass is obtained, and the color of the glass is reduced. Therefore, the refractive index (nd) can be obtained within the range of 163467.doc 201245078, and the Abbe number (vd) is small, the partial dispersion ratio (0g, F) is small, and the transparency with respect to visible light is high. Optical glass, and preforms and optical components using the optical glass. [Embodiment] The optical glass of the present invention contains 20.0% or more and 60.0% or less of the Si 2 component, and more than 20.0% and 50.0 % of the CaO component, based on the total mass of the glass of the oxide conversion composition. /〇Following, the content of the Nb205 component is 30.0% or less 'between the partial dispersion ratio (Gg, F) and the Abbe number (Vd), which satisfies (·〇.〇〇ΐ62χνί1+0.63822) in the range of vd$31. The relationship between (θ§, F) ^ (-0.00275xvd+0.68125) satisfies the relationship of 〇0.00162xvcl+0.63 822) $(0g,F) $(-0.00162xvd+0.64622) in the range of vd>31. By using the Si〇2 component and the CaO component in combination, and setting the contents in a specific range, a stable glass can be formed, and the Abbe number (vd) can be lowered and the color of the glass can be reduced. Further, by setting the content of the Nb205 component within a specific range, a lower Abbe number and a lower partial dispersion ratio ' can be obtained and the devitrification of the glass is reduced. Therefore, an optical glass having a refractive index (nd) within a desired range and having a small Abbe number (Vd), a small partial dispersion ratio (0g, F), and a high transparency with respect to visible light can be obtained, and A preform of the optical glass and an optical element are used. Wherein the first optical glass is a molar mass of the total composition of the glass in terms of oxide composition. / 〇 , , , , , , , , 合 合 合 合 合 合 合 合 合 合 合 合 合 合 合 合 合 合 合A desired high refractive index can be obtained by using one of the Ba 〇 component and the κ 2 〇 component, and a lower partial dispersion ratio (0g, F) can be obtained. At the same time, by using the Si〇2 component together with Ca0 to form 163467.doc •10·201245078, and the content of these is set within a specific range, coloring or devitrification is less likely to occur when the glass is reheated. Therefore, the refractive index (nd) can be obtained within a desired range, and the Abbe number (Vd) is small, the partial dispersion ratio (Qg, ρ) is small, and the transparency with respect to visible light is high, and has a higher An optical glass that is high in shape and a preform and an optical element using the optical glass. Further, in the second optical glass, by setting the content of the Si〇2 component, the Ca〇 component, and the Nb2〇5 component within a specific range, a higher refractive index can be obtained and a lower yield can be obtained. The number of shells or partial dispersion ratio, and the devitrification of the glass is alleviated. Therefore, 'a refractive index (nd) is obtained in a desired higher range, and the Abbe number (vd) is smaller, the partial dispersion ratio (eg, F) is smaller, and the transparency with respect to visible light is higher. Glass, and preforms and optical components using the optical glass. Hereinafter, the embodiment of the optical glass of the present invention will be described in detail, but the present invention is not limited to the following embodiments, and may be appropriately modified and implemented within the scope of the object of the present invention. Incidentally, the description of the description will be omitted as appropriate, but the purpose of the invention is not limited. [Glass Component] The composition range of each component constituting the optical glass of the present invention is as follows. In the present specification, the content of each component is, unless otherwise specified, «and is also expressed as % of the total mass of the glass in terms of oxide composition. Here, the "oxide-converting composition" is a composition in which an oxide, a composite salt, and a metal fluoride which are used as a raw material of the glass constituent component of the present invention are equivalent to being completely decomposed and converted into an oxide at the time of melting. 163467.doc 201245078, the total mass of the produced oxide is set to 100 mol%, and each component contained in the glass is expressed. <About essential components, arbitrary components>

The Si 2 component promotes stable glass formation and reduces the composition of devitrification (production of crystals) which is poor as an optical glass. In particular, by setting the content of the Si 2 component to 20.0% or more, it is possible to obtain a glass excellent in devitrification resistance without significantly increasing the partial dispersion ratio of the glass. Further, by this, devitrification or coloration at the time of reheating can be reduced. On the other hand, by setting the content of the §2 component to 60.0% or less, the refractive index of the glass is not easily lowered, whereby a desired higher refractive index can be easily obtained, and the glass can be suppressed. Part of the dispersion has increased. Further, by setting the content of the Si 2 component to 60.0% or less, the meltability of the glass can be favorably maintained. Therefore, the lower limit of the content of the component is preferably 20.0%, more preferably 21, still more preferably 24.0%, still more preferably 27.9%, most preferably 3〇%. Further, the upper limit of the content of the si 2 component is preferably 60%, more preferably 5 %, and most preferably 45.0%. As the Si02 component, si〇2, K2SiF6, Na2SiF6 or the like can be used as a raw material.

The CaO component is a component necessary for obtaining a glass having a low Abbe number and high devitrification resistance. In particular, by setting the content of the Ca0 component to more than 20.0%, an optical glass having a low Abbe number and high devitrification resistance can be obtained, and the solubility of the glass can be obtained. On the other hand, by setting the content of the Ca 〇 component to 50·0% or less ′, it is possible to suppress a decrease in the refractive index of the glass or an increase in the partial dispersion ratio ′ and to suppress the glass caused by the excessive content of the CaO component. Deterioration of resistance to devitrification. Moreover, by this, the devitrification or coloration when reheating 163467.doc 12 201245078 can be reduced. Therefore, the lower limit of the content of the CaO component is preferably set to be more than 20.0%, more preferably 24.0%, still more preferably more than 3〇%, and even more preferably 32.0. /. The best is 33.5%. Further, the upper limit of the content of the Ca 〇 component is preferably 50.0%, more preferably 45.0%, still more preferably 43.0% Å, most preferably 4 〇.〇〇/0. As the CaO component, CaC03, CaF2 or the like can be used as a raw material. In particular, in the first optical glass, it is preferable that the Ba 〇 component and the K 〇 〇 component are more than 0 〇 / 〇 and 20, 0% or less. By containing the total content in more than 〇%, a glass having a desired lower partial dispersion ratio can be obtained. On the other hand, by setting the total content to 20.0% or less, it is possible to suppress the deterioration of the devitrification resistance or the chemical durability caused by the excessive content of the components. Therefore, the lower limit of the molar and (BaO + hO) is preferably set to be more than 〇%, more preferably 0.5. /. And further preferably κο%. Further, the upper limit of the molar and (Ba〇+K2〇) is preferably set to 20.0°/. More preferably, it is 15%, and the best is 1〇 〇0/〇.

The Nb2〇5 component is a component which is resistant to devitrification of the glass of the South, and is a component which increases the refractive index of the glass and lowers the Abbe number and the partial dispersion ratio, and is an arbitrary component in the optical glass of the present invention. In particular, by setting the content of the Nb2〇5 component to 3 〇.% or less, the increase in the melting temperature at the time of glass production can be suppressed, and the devitrification caused by the excessive content of the Nb2〇5 component can be reduced. Therefore, the upper limit of the content of the Nb2〇5 component is preferably set to 3〇%, more preferably 2〇.〇%, and most preferably 1 5·〇%. Further, the Nb2〇5 component may not be contained, but by containing more than 〇% of the Nb2〇5 component, the refractive index of the high glass can be & and the abebe can be further lowered, and the glass can be lowered. Partial dispersion ratio. Further, by containing more than 〇% of the Nb2〇5 component, the devitrification resistance of the glass 163467.doc 201245078 can be improved, and the extrusion formability of the intergranular glass can be improved. Therefore, the lower limit of the amount of the Nb2〇5 component is preferably set to be more than 〇% ‘, preferably 3, preferably 4.0%, and the seedling is preferably 5.0/. The best is 6 〇%. The Nb2〇s component uses Nb»2〇5 or the like as a raw material. The 2% knife system raises the refractive index of the glass, and reduces the Abbe number. The knife is an arbitrary component of the optical glass of the present invention. In particular, by setting the content of the Ti〇2 component to 2% or less, it is more preferable to reduce the color of the glass and increase the internal transmittance of the glass by the content of the T1〇2 component. When it is set to 10.〇% or less, since the partial knife width ratio 4 does not easily rise, it is possible to easily obtain a low partial dispersion ratio close to the regular line. The upper limit of the content of the & 'Ti〇2 component is preferably 20·0/〇', more preferably 15% by weight, and even more preferably less than or equal to 10.0%, and even more preferably 95%. The best is 9 〇〇 / 〇. On the other hand, the viewpoint of obtaining a lower partial dispersion ratio or the viewpoint of reducing coloration is higher than (4) without (10), but a higher refractive index or lower Abbe number is obtained, and the tolerance is improved. From the viewpoint of permeability, the lower limit of the content of the Ti 2 component is preferably set to more than 〇%, more preferably from 1 to 0%, still more preferably 3.0. /〇, the best is 4.5%.

As the T1〇2 component, Ti〇2 or the like can be used as a raw material. In particular, in the second optical glass, it is preferable that the sum of the Nb2〇5 component and the butadiene2 component is 1%·〇% or more and 40.0% or less. In particular, it is possible to obtain a desired higher refractive index and lower by increasing the content of the Nb2〇5 component and the Ti〇2 component by increasing the refractive index and lowering the Abbe number. Optical glass of Abbe number. On the other hand, since the sum is 163467.doc •14·201245078 40.0〇/〇 or less, since the devitrification caused by the 箄忐八田通 is reduced, a stable glass with higher devitrification property can be obtained. , Karma. Therefore, the molar and more preferably 12·0%, the aspect-in, the molar and the better is 30. 〇%, and the lower limit of the (Nb205+Ti02) is preferably set to 1〇〇%, and more preferably It is 14.0%, and the best is 15%. Further, the upper limit of (Nb2〇5+Ti〇2) is preferably set to 4〇 and more preferably 25.0%, and most preferably 2〇 〇0/. .

The BaO component improves the refractive index of the φ ^ 坂碉 of the glazed cup, reduces the partial dispersion ratio of the glass, and improves the composition of the glass. In particular, by setting the content of the Ba〇 component to 25.0% or less, more preferably 2% by weight or less, deterioration of devitrification resistance or chemical durability due to excessive inclusion of the secret component can be suppressed. Therefore, the upper limit of the content of the bismuth component is preferably set to 25.0%, more preferably 20.0/Torr, still more preferably 15%, and most preferably (7) (4). Further, since the Ba〇 component is an optional component, it may or may not be contained, but it can be easily degraded or devitrified by containing Ba〇 into a knife, and the desired property can be easily achieved. Higher refractive index and lower partial dispersion ratio. Further, by this, the devitrification or coloring upon reheating can be reduced. Therefore, the lower limit of the content of the 'Ba0 component' is preferably more than 〇%', more preferably 〇, and still more preferably 1.0%. On the other hand, as the Ba〇 component, Ba(N〇3)2 or the like can be used as a raw material. In the optical glass of the present invention, the sum of the content of the Nb2〇5 component and the Ba0 component is preferably 〇1〇〇 or more with respect to the sum of the content of the Ti〇2 component and the Ca〇 component. In this way, the content of the TiO 2 component and the Ca 〇 component as a component for increasing the partial dispersion ratio is increased as the content of the component 1 / 2 〇 5 component and the BaO component which lowers the partial dispersion ratio component, and thus the desired content can be obtained. Lower 163467.doc 15 201245078 Partial dispersion ratio of optical glass "Therefore, the lower limit of the molar ratio of the molar ratio (Nb205 + Ba0) / (Ti02 + Ca0) is preferably set to 〇 _! 〇〇, more The best is 0.120, and even more preferably mo, the best is 〇14〇. On the other hand, the upper limit of the molar ratio (Nb2〇5+BaO)/(Ti〇2+Ca〇) is not particularly limited, but the optical glass of the present invention is mostly the molar ratio (Nb2〇5+Ba〇). /(Ti〇2 + Ca〇) is 1_000 or less, more specifically 〇7〇〇 or less, and more specifically 0.400 or less. The optical glass of the present invention preferably has a molar ratio of oxide conversion

Ti〇2/Nb2〇5 is 5·〇〇 or less. Thereby, the Abbe number of the glass can be adjusted within a desired range, and the partial dispersion ratio becomes low, so that an optical glass having a desired Abbe number and a partial dispersion ratio can be obtained. At the same time, an optical glass having less coloration can be obtained. The upper limit of the molar ratio of the composition of the oxide to the composition of the oxide ratio is preferably set to 5 〇〇, more preferably 4.00, still more preferably 3. 〇〇, more preferably 2 5 〇, and even more preferably 2.00. In particular, in the first optical glass containing at least one of the Ba0 component and the ΚΖ0 component as an essential component, it is preferable to set the Ti〇2/Nb2〇s to 2. 〇〇The following.

The Ll2 bismuth component is a component of the optical glass of the present invention which increases the (tetra) property of the glass and lowers the component of the glass. In particular, by setting the content of the component (10) to 25%, it is possible to suppress the low p of the refractive index, and at the same time, reduce the whitening caused by the excessive content of the component of Li2, or the whitening at the time of re-heating or reheating. Crystallization precipitates and improves the durability of the glass. Therefore, the upper limit of the content of the '(10) component is preferably set to be 25%, more preferably 17, and more preferably 12, and further 163467.doc S'-16-201245078 9.5%, most Preferably, 5.0% e Li2〇 component can be used as a raw material using U2C〇3, LiN〇3, uf, and the like.

The Na2〇 component is a component which improves the smelting property of the glass, and at the same time, reduces the component of the glass transition point, and is an arbitrary component in the optical glass of the present invention. In particular, by setting the content of the NkO component to 25 〇% or less, the refractive index is not easily lowered, and chemical durability is not easily deteriorated. The devitrification resistance at the time of glass formation can be improved, and the devitrification at the time of reheating can be reduced. Or coloring. Therefore, the upper limit of the content of the NazO component is preferably set to 25, more preferably 15.0%, still more preferably 1% by weight, and most preferably 5% by weight. The Naz〇 component can be made of NaWO3, NaN〇3, NaF, Na2SiF6 or the like as a raw material. The composition adjusts the meltability of the glass and lowers the composition of the glass transition point, and is an optional component in the optical glass of the present invention. In particular, by setting the content of the Κ2〇 component to 25.0% or less, the devitrification resistance at the time of glass formation can be improved, and the devitrification or coloration at the time of reheating can be reduced. Therefore, the upper limit of the content of the κ 2 〇 component is preferably 25.0%, more preferably 20.0%, still more preferably 15.0%, and most preferably ίο. 0%. Further, the component a may not be contained in view of obtaining a glass having more extrusion moldability, but the lower limit of the content may be set to more than 0 because it has a function of further reducing the partial dispersion ratio. %, more preferably 〇.5〇/. And even better! 〇0/. . The κ 2 〇 component can be used as a raw material such as K2C03, ΚΝ〇3, KF, KHF2, K2SiF6 or the like.

The CszO component lowers the composition of the glass transition point and is an optional component in the optical glass of the present invention. In particular, by setting the content of the CS2 bismuth component to 1 〇.〇% or less, the devitrification of the glass caused by the excessive content of the Cs2 bismuth component can be reduced. Therefore, the upper limit of the content of the 'Cs2〇 component is preferably set to 1〇%, more preferably 163467.doc •17· 201245078

The Cs2〇 component can be used as Cs2C〇3, csNC) 5.0°/. And further preferably 3.0%. Etc. as a raw material. In the optical glass of the present invention, it is preferable that the sum of the contents of Rn2 (10) (wherein, the group selected from the group consisting of Li 'Na, κ and Cs) is 30.0%. In particular, the desired high fold (4) can be easily obtained by setting the moir and the following, and (4) reducing the glass opacity. Therefore, the upper limit of the molar content of the Rn2〇 component is preferably set to 30.0/. More preferably, it is 2〇 〇%, and further preferably 〇%, and more preferably 7·0°/〇 ’ is preferably 5.〇〇/0.

The MgO component is a component which lowers the glass transition temperature of the glass and is an optional component in the optical glass of the present invention. In particular, by setting the content of the Mg bismuth component to 20.0%, the decrease in the refractive index of the glass can be suppressed and the devitrification resistance of (4) can be improved. Moreover, by this, devitrification or coloring at the time of reheating can be reduced. Therefore, the upper limit of the content of the Mg 〇 component is preferably 2% ,%, more preferably 10.0%, and most preferably 5.0%. As the MgO component, Mg〇, MgC〇3, MgFz or the like can be used as a raw material.

The SrO bismuth is a component which increases the refractive index of the glass and increases the resistance to devitrification of the glass, and is an optional component in the optical glass of the present invention. In particular, by setting the content of the SrO component to 20.0% or less, deterioration of chemical durability of the glass can be suppressed. Therefore, the upper limit of the content of the Sr0 component is preferably set to 2% ,%, more preferably 15.0%, and most preferably 1% 〇%. As the Sr〇 component, Sr (N〇丄, S r F2 or the like can be used as a raw material.

ZnO is an ingredient which increases the resistance to devitrification of glass and lowers the glass transition point, and is an optional component in the optical glass of the present invention. In particular, by setting the content of the Zn〇 163467.doc $ _ 18· 201245078 component to 3 〇.〇% or less, the glass can be reduced in reheating during reheating, and the chemical durability of the glass can be improved. Further, by this, the devitrification or coloring at the time of reheating can be reduced. Therefore, the upper limit of the content of the Zn 〇 component is preferably set to 30.0%, more preferably 2% by weight, still more preferably 16% by weight, and most preferably 〇, since the Zn 〇 component is an optional component, The content of the Zn 〇 component may preferably be set to be more than 〇%, more preferably, from the viewpoint of obtaining a higher resistance to devitrification and a lower glass transition point. 0.5% 'and thus better. As the raw material of zn〇, ZnO, ZnF2 or the like can be used. In the optical glass of the present invention, the R〇 component (wherein R is selected from the group consisting of Zn, Mg, Ca, Sr, and Ba) improves the resistance to devitrification of the glass and is adjusted. A useful component of the refractive index. In particular, by setting the content of the RO component to 20.0% or more, the devitrification resistance of the glass can be improved. When the total content of the RO components is too large, the devitrification resistance of the glass is reversed. It is prone to deterioration and the chemical durability of the glass also becomes prone to deterioration. Therefore, the lower limit of the total content of the R 〇 component is preferably set to 20.0%, more preferably 25% by weight, still more preferably 3 〇%, and most preferably more than 35.0%. Further, the upper limit of the total content of the R 〇 component is preferably set to 60.0%, more preferably 55.0%, and most preferably 50.0%. The 2〇5 component is a component which improves the stability of the glass and is an optional component in the optical glass of the present invention. In particular, by setting the content of the P2〇s component to 30.0% or less, the devitrification caused by the excessive content of the P2〇5 component is reduced, so that the stability of the glass can be improved. Therefore, the upper limit of the content of the cerium 5 component is preferably set to preferably 3 〇 % ' more preferably 2 〇 〇 %, and most preferably 163467.doc 201245078 10.0%. As the p2〇5 component, A1(P〇3)3, Ca(p〇3)2, Ba(p〇3)2, bp〇4, H3p〇4 or the like can be used as a raw material. The B2〇3 component is a component which promotes stable glass formation and improves resistance to devitrification, and which improves the meltability of glass, and is an arbitrary component in the optical glass of the present invention. In particular, by reducing the content of the yttrium 3 component to 4 〇·〇% or less, the decrease in the refractive index can be suppressed, whereby a desired higher refractive index can be obtained, and at the same time, the partial dispersion ratio of the glass can be suppressed from increasing. . Further, by this, the devitrification of the glass during reheating can be reduced. Therefore, the upper limit of the content of the component (^) is preferably 40.0%, more preferably 30.0%, still more preferably 2% by weight, still more preferably 15.0%, most preferably 10.0. / (^ Further, since the β2〇3 component is an optional component, it may not be contained, but by containing more than 〇% of the Β2〇3 component, the devitrification resistance and the meltability of the glass can be improved. Therefore, the β2〇3 component is The lower limit of the content is preferably set to more than 0%, more preferably 丨〇%, and most preferably 2% 。%. Β2〇3 may be used as a raw material using Η3Β〇3, Na2B407, Na2B4O7.10H2O, ΒΡ04 or the like.

The Ge 〇 2 component is an arbitrarily formed knives in the optical glass of the present invention by increasing the refractive index of the glass, stabilizing the glass, and reducing the devitrification component during molding. In particular, by setting the content of the Ge 〇 2 component to 2% by weight or less, the amount of the Ge 〇 2 component which is expensive is reduced, so that the material cost of the glass can be reduced. Therefore, the upper limit of the content of the 'Ge〇2 component is preferably 2% ,%, more preferably 1 G.0%' and still more preferably 5% by weight, and most preferably 3 (%). & 〇 2 component Ge 〇 2 or the like can be used as a raw material. Γ2〇3 component, La2〇3 component 'Gd2〇3 component and Yb2〇3 component are components which increase the refractive index of glass and reduce the partial dispersion ratio, and are any of 163467.doc -20- 201245078 optical glass of the present invention. ingredient. In particular, by setting the contents of the Υ2〇3 component, the La2〇3 component, the Gd2〇3 component, and the Yb2〇3 component to 15% by weight or less, the devitrification resistance of the glass can be improved, and the glass Abe can be suppressed. The number has risen. Therefore, the upper limit of the content of each of the Y203 component, the La203 component, the Gd203 component, and the Yb2〇3 component is preferably 15.0%, more preferably 1% by weight, still more preferably 7.0%, and most preferably 4.2. /❶. Γ2〇3, %, La2〇3, La(N〇3)3 XH20 (X is an arbitrary integer), Gd2〇3, GdF3 can be used for the Y2〇3 component, the La2〇3 component, the Gd2〇3 component, and the Yb2o3 component. , Yb2〇3, etc. as raw materials.

The Ta2〇5 component is a component of the optical glass of the present invention which is a component of the optical glass of the present invention which is a component which increases the refractive index of the glass, lowers the Abbe number and partial dispersion ratio of the glass, and improves the resistance to devitrification of the glass. In particular, by setting the content of the Ta2〇5 component to 15.0% or less, the amount of the τ&2〇5 component which is a rare mineral resource is reduced, and at the same time, the glass is easily melted at a lower temperature, so that the glass can be reduced. Production costs. Further, by setting the content of the Ta2〇5 component to 15.0% or less, it is possible to reduce the devitrification of the glass caused by the excessive content of the component of the dinosaur. Therefore, the upper limit of the content of the 'Ta2〇5 component is preferably set to 15.0%, more preferably 1% 〇%' is preferably 5%. As the Ta2〇5 component, Ta205 or the like can be used as a raw material.

The Bi2〇3 component increases the refractive index of the glass and lowers the Abbe number, and lowers the composition of the glass transition point, and is an arbitrary component in the optical glass of the present invention. In particular, by setting the content of the B2 2 〇 3 component to 15.0% or less, the partial dispersion ratio of the glass can be prevented from rising. Further, by setting the content of the Bi2〇3 component to 15.0 Å/〇 or less, the color of the glass can be reduced, and the transmittance of the glass can be increased by 163467.doc • 21 · 201245078. Therefore, the upper limit of the content of the B gentleman and the eighty-three knives is preferably set to 15.0%, more preferably 1 〇 〇 0 / the maximum occupancy is 5.0%. Bi2〇3 ingredients can be used

Bi2〇3 is used as a raw material. The W〇3 component is a component of the optical glass of the present invention which increases the refractive index of the glass and lowers the Abbe number, and improves the devitrification resistance of the glass. . In particular, by setting the content of the wo3 component to 20.0% or less, the partial dispersion ratio of the glass can be prevented from rising. Further, by setting the content of the W〇3 component to 2 Å or less, the color of the glass can be reduced, and the internal transmittance of the glass can be improved. Therefore, the upper limit of the content of the w〇3 component is preferably set to 20.0. /. ‘More preferably 1〇 〇%, optimally 5%%. The w〇3 component can use W03 or the like as a raw material.

The Te〇2 component increases the refractive index of the glass, lowers the partial dispersion ratio of the glass, and lowers the composition of the glass transition point, and is an arbitrary component in the optical glass of the present invention, especially by setting the content of the Te〇2 component to 3〇. Below 〇%, the color of the glass can be reduced, and the transmittance of the glass with respect to visible light can be improved. Further, by reducing the use of the expensive Te〇2 component, a glass having a lower material cost can be obtained. Therefore, the upper limit of the content of the Te〇2 component is preferably set to 30.0%, more preferably 2% by weight, and most preferably 丨〇%. As the Te〇2 component, Te〇2 or the like can be used as a raw material.

The Zr〇2 component is an optional component in the optical glass of the present invention which is a component which increases the refractive index and Abbe number of the glass, lowers the partial dispersion ratio, and improves the devitrification property. In particular, the devitrification of the glass can be reduced by setting the content of the ZrO 2 component to 15.0 ° / 〇 or less, and a more homogeneous glass can be easily obtained. Therefore, the upper limit of the content of the 'Zr〇2 component is preferably set to 15.0%, more preferably 163467.doc -22-s 201245078 12.0% 'Best is 1 〇Qin or no Zr〇2 component By containing more than 〇% of the Zr〇2 component, the refractive index and Abbe number of the glass can be increased and the partial dispersion ratio of the glass can be easily further reduced. Further, by this, the devitrification or coloring upon reheating can be reduced. Therefore, the lower limit of the content of the ha component is preferably set to be more than 〇%, more preferably i is, and still more preferably 2·0°/〇. As the ZrO 2 component, Zr 〇 2, ZrF 4 or the like can be used as a raw material. The Α1ζ〇3 component is a component which improves the chemical durability 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, by setting the content of the Ah 3 component to 15% or less, the devitrification caused by the excessive content can be reduced. Further, by this, devitrification or coloration at the time of reheating can be reduced. The upper limit of the content of the *匕' Al2〇3 component is preferably set to 15.0%', more preferably 10.0%, most preferably 5%. As the Al2〇3 component, Al2?3, Al(OH)3, A1F3 or the like can be used as a raw material.

The ShO3 component promotes defoaming of glass and clarifies the composition of the glass, and is an optional component in the optical glass of the present invention. By setting the content of the Sfc>2〇3 component to i 〇% or less with respect to the total mass of the glass, it is possible to prevent excessive foaming when the glass is melted, and it is possible to make the Sb203 component difficult to melt with the melting equipment (especially Pt, etc.) Precious metal) alloyed. Therefore, the upper limit of the content of the Sb2〇3 component is preferably set to 1.0%, more preferably 0.8%, and still more preferably 〇.6%. However, in the case where the influence of the optical glass on the environment is emphasized, it is preferred that the Sb203 component is not contained. As the raw material of Sb2〇3, Sb2〇3, sb2〇5, Na2H2Sb2〇7 5H20 or the like can be used. Further, the component for clarifying the glass and defoaming is not limited to the above sb2〇3 component, and a clarifier or a defoaming agent known in the field of glass production, or a combination of 163467.doc • 23-201245078 may be used. <About the component which should not be contained> Next, the component "which should not be contained in the optical glass of the present invention" and the component containing an undesirable component will be described. In the optical glass of the present invention, other components may be added as needed within the range of the characteristics of the non-destructive glass. However, in addition to Ti, Zr, and Nb, each transition metal component such as v, Cr, Mn, c〇, sin, Cu, Ag, and Mo has a coloring of the glass even when it is contained in a small amount alone or in combination. Since the light of the wavelength of the characteristic of the visible region is absorbed, it is preferable that the optical glass having a wavelength of the visible region is substantially not contained. Further, lead compounds such as PbO and arsenic compounds such as AS2〇3, and various components of butyl sulfonium, Cd, hydrazine, Os, Be, and Se have been used as harmful chemical materials in recent years, and tend to be used not only in the manufacture of glass. In the step, measures for environmental measures are required in the processing steps and processing up to the time of product preparation. Therefore, when it is important to pay attention to environmental influences, it is preferable that these are not substantially contained except for inevitable mixing. Thereby, the optical glass is made substantially free of substances that pollute the environment. Therefore, the optical glass can be manufactured, processed, and discarded without taking special measures for environmental countermeasures. It is preferably used as the glass of the optical glass of the present invention, and its composition is based on the total mass of the glass of the composition in terms of oxide. /Kou _ Fu Yu / 0 is not, so it is not directly expressed as quality. /. It is described that the components present in the glass composition satisfying the characteristics required in the present invention are formed by the composition of the oxides in the form of oxides in the form of _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ , roughly take the following values. SiO2 component 15.0 to 45.0% by mass and CaO component 15.0 to 35.0% by mass and

Nb205 component 0 to 5 5.0% by mass and/or TiO 2 component 0 to 20.0% by mass and/or BaO component 0 to 45.0% by mass and/or Li20 component 0 to 10.0% by mass and/or Na20 component 0 to 20.0% by mass and/or Or K20 component 0 to 3 0.0% by mass and/or Cs20 component 0 to 25.0% by mass and/or MgO component 0 to 5.0 mass ° / 〇 and / or SrO component 0 to 25.0 mass ° / 〇 and / or ZnO component 0 ~ 25.0% by mass and/or P2〇5 component 〇~3 0.0% by mass and/or B2〇3 component 0 to 30.0% by mass and/or Ge02 component 0 to 20.0% by mass and/or Y2〇3 component 〇~3 0.0 mass % and / or La203 component 0 to 40.0% by mass and / or Gd203 component 0 to 40.0% by mass and / or Yb203 component 0 to 40.0 mass ° / 〇 and / or Ta205 component 0 to 50.0% by mass and / or Bi2 〇 3 component 〇~50.0 mass ° / 〇 and / or W03 composition 0 ~ 30.0% by mass and / or 163467.doc -25- 201245078

Te02 component 0 to 45.0% by mass and/or Zr02 component 0 to 20.0% by mass and/or Al2〇3 component 0 to 20.0% by mass and/or Sb203 component 0 to 3.0 mass. / 〇 In particular, the composition of each component present in the first optical glass represented by mass % is approximately the following value in terms of oxide conversion composition.

SiO2 component 15.0 to 45.0% by mass and CaO component 15.0 to 35.0% by mass and

Nb205 component 0-5 5.0% by mass and/or TiO2 component 0 to 10.0% by mass and/or BaO component 0 to 3 5.0% by mass and/or Li20 component 0 to 10.0% by mass and/or Na20 component 0 to 20.0% by mass and/or / or K20 component 0 to 30.0% by mass and / or Cs20 component 0 to 25.0 mass ° /. And/or MgO component 0 to 5.0% by mass and/or SrO component 0-25.0% by mass and/or ZnO component 0 to 25.0% by mass and/or P2〇5 component 〇~3 0.0% by mass and/or B2〇3 component 0 to 30.0% by mass and/or Ge02 component 0 to 20.0% by mass and/or Y2〇3 component 〇~30.0% by mass and/or La203 component 0 to 40.0 mass °/〇 and/or 163467.doc •26·201245078

Gd203 component 0 to 40.0% by mass and/or Yb203 component 0 to 40.0% by mass and/or Ta205 component 0 to 50.0% by mass and/or Bi203 component 0 to 50.0% by mass and/or W03 component 0 to 30.0% by mass and/or Te02 component 0 to 45.0% by mass and/or Zr02 component 0 to 20.0% by mass and/or Al2〇3 component 0 to 20.0% by mass and/or Sb203 component 0 to 3.0% by mass, and each of the second optical glass The composition represented by the mass % of the component is approximately the following value in terms of the oxide conversion composition.

SiO2 component 15.0 to 45.0% by mass and CaO component 15.0 to 35.0% by mass and

Nb205 component 0 to 5 5.0% by mass and/or TiO 2 component 0 to 20.0% by mass and/or BaO component 0 to 45.0% by mass and/or Li20 component 0 to 10.0% by mass and/or Na20 component 0 to 20.0% by mass and/or Or K20 component 0 to 30.0% by mass and/or Cs20 component 0 to 25.0% by mass and/or MgO component 0 to 5.0% by mass and/or SrO component 0 to 25.0% by mass and/or ZnO component 0 to 25.0% by mass and/or Or 163467.doc •27- 201245078 P2〇5 component 0~30.0% by mass and/or Β203 component 〇~3〇.〇% by mass and/or Ge02 component 〇~20.0% by mass and/or Y2O3 component 0~30.0% by mass And / or La203 ingredients 〇 ~ 40.0 quality. /〇 and / or Gd203 composition 〇 ~4 〇. 〇 quality. /. And / or Yb203 composition 〇 ~ 40.0 mass. /. And / or Ta205 ingredients 〇 ~ 5 〇. 〇 quality. /. And / or Bi2 〇 3 ingredients 〇 ~ 50.0 mass. /〇 and / or W03 composition 〇 ~3 〇. 〇 mass% and / or Te02 composition 〇 ~ 45.0 mass 0 / 〇 and / or Zr 〇 2 components 〇 ~ 20. 〇 mass% and / or AI2O3 composition 〇 ~ 20.0 quality . 〇 / / 3.0 3.0 3.0 3.0 3.0 3.0 3.0 [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ [ 光学 光学 光学 光学 光学 光学 光学 光学 光学 光学 光学 光学 光学The prepared mixture is poured into platinum crucible, quartz crucible or alumina crucible for coarse melting, and then placed in a crucible, a platinum crucible, a platinum alloy crucible or a crucible, at 1100 to 1400. (: The temperature range is melted for 3 to 5 hours, stirred and homogenized, defoamed, etc., and then lowered to a temperature of ~13 〇〇, and then finely mixed, the veins are removed, and the pray is poured into the mold. The optical portion is formed by the cold portion. <Physical properties: > 163467.doc -28^ 201245078 The optical glass of the present invention preferably has a specific refractive index and dispersion (Abbe number). More specifically, The lower limit of the refractive index (nd) of the optical glass of the present invention is preferably set to 1.70, more preferably 1.75, most preferably 178. On the other hand, the upper limit of the refractive index (nd) of the optical glass of the present invention is not In particular, 'more than about 2.20 or less' is more specifically 2.1 Å or less, and more specifically 2.00 or less, and more specifically 195 or less. Further, the Abbe number (vd) of the optical glass of the present invention. The upper limit of the optical glass of the present invention is preferably set to 4 Å, more preferably 38, and most preferably 35. On the other hand, the lower limit of the Abbe number (vd) of the optical glass of the present invention is not particularly limited, and is usually about 2 Å or more. More specifically, it is 25 or more, and more specifically 27 or more. By these, optical The degree of freedom in design is expanded, and further, even if the thinning of the element is sought, a large amount of light can be obtained. Further, the optical glass of the present invention has a lower partial dispersion ratio (eg, F). More specifically, Between the partial dispersion ratio (0g, F) and the Abbe number (vd) of the optical glass of the present invention, it satisfies (_〇〇〇162xvd+O.63822)S(0g,F)$(- in the range of Vd$31. The relationship of 0.00275xvd+0.68125), and the range of vd > 31 satisfies the relationship of (-〇.〇〇i62xvd+O.63822)S(0g,F)g (-0_00162xvd+0.64622). An optical glass having a partial dispersion ratio (eg, F) close to a regular line, thereby reducing the chromatic aberration of the optical element formed by the optical glass. Here, the partial dispersion ratio of the optical glass at Vd$31 (0g, The lower limit of F) is preferably (_0.00162x vd+0.63822), more preferably (_0.00162xvd+〇.63922), and most preferably (-0.00162x vd+0.64022). On the other hand, the optical glass of 'Vd$31 The upper limit of the partial dispersion ratio (0g, F) is preferably (_〇.〇〇275xvd+0.68125), more preferably I63467.doc •29- 201245078 (•0.00275xvd+0.680 25), the best is (-〇.〇〇275xvd+0.67925). Further, the lower limit of the partial dispersion ratio (0g, F) of the optical glass at vd>3 1 is preferably (-0.00162xvd+0.63822), Good (-0.00162> <vd+0.63922), the best is (-0.00162xvd+0.64022). On the other hand, the upper limit of the partial dispersion ratio (〇g, F) of the optical glass at vd > 31 is preferably (-0.00162xvd + 0.64622), more preferably (-0.00162xvd + 0.64522), and most preferably (-0 ·00162χ vd+0.64422). Furthermore, especially in the region where the Abbe number (vd) is small, the partial dispersion ratio (0g, F) of the ordinary glass is higher than the regular line value, and the partial dispersion ratio of the ordinary glass (eg, F) and Abbe The relationship of the number (vd) is represented by a curve. However, since the approximation of the curve is difficult, in the present invention, a straight line having a different slope using vd = 3 1 as a boundary indicates that the partial dispersion ratio (0g, F) is lower than that of ordinary glass. Further, the optical glass of the present invention preferably has less coloration. In particular, when the optical glass of the present invention is expressed by a transmittance of glass, a wavelength of 10% of the spectral transmittance (λ7〇) of the sample having a thickness of 10 mm is 500 nm or less, more preferably 470 nm or less, and even more preferably Below 450 nm, the best is below 430 nm. Further, when the optical glass of the present invention is expressed by the transmittance of glass, the wavelength (λβο) at which the spectral transmittance is 80% is 560 nm or less, more preferably 540 nm or less, and most preferably 520. Below nm. Further, the optical glass of the present invention shows a wavelength (λ5) of a spectral transmittance of 5% of a sample having a thickness of 10 mm of 420 nm or less, more preferably 400 nm or less, and most preferably 380 nm or less. Thereby, the absorption end of the glass is located in the vicinity of the ultraviolet region, and the transparency of the glass in the visible region is improved, so that the optical glass can be preferably used as a material of an optical element such as a lens. 163467.doc -30· 201245078 Further, the optical glass of the present invention is comparative. Good extrusion molding is good. That is, the optical glass of the present invention is preferably obtained by dividing the transmittance of the light having a wavelength of 587.56 nm (d line) of the test piece after the reheating test (2) by the transmittance of the d line of the test piece before the reheating test. The value is 〇95 or more. Further, it is preferable that the difference between the transmittance of the test piece before the reheat test (2) and the wavelength of λ7 即 which is 7 〇 %, and the test piece after the reheat test is 2 〇 nm or less. Therefore, even if the reheating test of the false twist reheating extrusion process is not easy to cause devitrification and coloring, the light transmittance of the glass is not easily lost, so that the glass can be easily represented by reheat extrusion processing. Reheat treatment. Namely, since an optical element having a complicated shape can be produced by extrusion molding, it is possible to manufacture an optical element which is inexpensive and has good productivity. Here, the lower limit of the value obtained by dividing the transmittance of the light ray (d line) of the test piece after the reheating test (2) by the transmittance of the test piece before the reheating test (2) is preferably It is preferably set to 〇95, more preferably 〇%, most preferably 0.97... The upper limit of the difference between the test piece before the reheat test (2) and the λ7 of the test piece after the reheat test (2) is preferably Set to 2 〇 nm 'more preferably 18 nm, preferably 16 nm. The 'reheat test (2) is carried out by reheating the test piece 15 mm x l5 mm x 30 mm, starting from room temperature for 150 minutes To the transfer temperature of each sample (such as high temperature, the glass transition temperature (Tg) of the above optical glass is higher than 8 (the temperature of rc is kept for 3q minutes, and then naturally cooled to normal temperature). The surface was polished to a thickness of 10 mm and visually observed. [Preform and optical component] 163467.doc 201245078 The optical glass produced can be extruded by a die such as reheat extrusion or precision extrusion. Forming means to produce a glass formed body β, that is, light The glass is used to form a preform for extrusion molding, and the preform is subjected to reheat extrusion molding, followed by polishing to produce a glass molded body or, for example, precision extrusion of a preform produced by polishing. The glass molded body is formed by molding, and the means for producing the glass molded body is not limited to these means. The glass molded body thus produced is useful for various optical elements, and 'preferably used for optics such as lenses or iridium. The use of the element, whereby the blurring of the color caused by the chromatic aberration in the transmitted light of the optical system provided with the optical element is alleviated. Therefore, when the optical element is used in a camera, it can be more correctly displayed. When the optical element is used in a projector, the desired image can be projected with great excitement. [Embodiment] Embodiments of the present invention (No. ^No.y) and comparative examples (Ν〇Α~n〇D) composition, and refractive index (nd), Abbe number (Vd), partial dispersion ratio (four), F), spectral transmittance show 5%, 70%, and 80% wavelength %, ^, ^), to The variation of the transmittance before and after the reheating test (II) is shown in Table 表 to Table 9 ^, and Example 42 is cited as an example of the first optical glass. ' Further, Example 1 30 and 36 to 57 4 to 11, 13, 14, 16 to 20, and 23 are examples of the second optical glass. The following examples are merely illustrative, and the present invention is not limited to the examples. The glass of the examples of the invention and the comparative examples are each selected from the respective oxides, hydroxides, carbonates, nitrates, fluorides, hydroxides, and 163467.doc •32·201245078 ordinary optical glass such as acid-inhibiting compounds. The high-purity raw materials used in the materials are used as raw materials of the respective components, and are weighed so as to be in proportion to the composition of each of the examples and the comparative examples shown in Table 9, and are uniformly mixed and then put into the time. In the exhaustion, according to the melting difficulty of the glass composition, it is melted in an electric furnace at a temperature of 1100 to 1400 ° C for 3 to 5 hours, and the mixture is homogenized. After defoaming, the temperature is lowered to! Hey ~! After 300 ° C & search and homogenization, it was cast into a mold and slowly cooled to prepare a glass. Here, the refractive index (nd), the Abbe's number (Vd), and the partial dispersion ratio (eg, F) of the glass of the examples and the comparative examples were measured based on the Sakamoto Optical Glass Industrial Standard JOGIS01-2003. Further, for the values of the obtained Abbe number and partial dispersion ratio (0g, F), the intercept in the relational expression (eg, F) = -axvd + b at a slope a of 0.00162 and 0.00275 is obtained. b» In addition, the glass used in the measurement was treated with a slow cooling rate of _25 ° c / hr and was treated by a slow cooling furnace. Further, the transmittance of the glass of the examples and the comparative examples was measured in accordance with the Japan Optical Glass Industry Association specification JOGIS02. Further, in the present invention, the presence or absence of the color of the glass is determined by measuring the transmittance of the glass. Specifically, for a parallel surface-polished product having a thickness of 10 ± 0.1 mm, the light transmittance of 200 to 800 nm is measured in accordance with JIS Z8722', and λ5 (wavelength at a transmittance of 5%) and λ7 〇 (transmittance 70%) are obtained. The wavelength of time) and x8G (wavelength at 80透过/〇 transmittance). Further, the change in transmittance before and after the reheating test of the glass of the examples and the comparative examples was carried out as follows: The light of the test piece after the reheating test (2) was 587.56 nm (d 163467. Doc 33· 201245078 line) The transmittance obtained by dividing the transmittance of the d-line of the test piece before the reheating test is the glass before and after the reheating test (2). According to the specifications of the Japan Optical Glass Industry Association J〇GIS02-2003 And proceed. Specifically, for the opposite surface parallel polishing product having a thickness of l〇±〇.l mm, the spectral transmittance of the 丄 line is measured according to JIS Z8722, and the d-line transmittance after the reheating test (2) is obtained. The d-line transmittance before the (1) test was evaluated for the change in the maximum transmittance before and after the reheat test (2). On the other hand, the transmittance of the test piece before the reheating test (II) becomes the wavelength of 70 / ❶, that is, the difference between λ7 〇 and the λ7 试验 of the test piece after the reheating test, for the glass before and after the reheating test (2) Using the above test method, 7 人 (wavelength at 70% transmittance) was obtained, and the difference between λ7 试验 of the test piece before the reheat test (2) and λ 70 of the test piece after the reheat test (2) was evaluated. Here, the 'reheating test (2) is carried out by placing a test piece of 15 mm x 15 mm x 30 mm on a concave refractory and placing it in an electric furnace for reheating 'from normal temperature for 15 minutes to a temperature The transfer temperature (TS) of the sample was 80. (: the temperature (the temperature in the refractory), after holding at this temperature for 30 minutes, cooling to normal temperature, and taking it out of the furnace, in order to be able to observe inside, the opposite surfaces were ground to a thickness of 10 mm. Thereafter, the ground glass sample was visually observed. 163467.doc 9 -34· 201245078 [Table 1] Example 1 2 3 4 5 6 7 8 Si02 33.655 33.655 33.655 33.655 36.655 33.655 33.655 36.655 CaO 37.562 37.562 37.562 37.562 37.562 37.562 37.562 37.562 Nb205 7.204 7.204 7.718 7.718 7.718 9.218 9.218 9.218 Ti02 6.990 6.990 8.490 8.490 8.490 6.990 6.990 6.990 Li20 Na2〇K20 3.000 3.000 3.000 MaO SrO BaO 3.000 3.000 2.000 3.000 2.000 ZnO 1.961 1.961 1.961 1.961 1.961 1.961 1.961 1.961 B2O3 4.699 4.699 4.699 4.699 2.699 4.699 4.699 2.699 Y7.〇3 La2〇3 0.514 0.514 Gd2〇3 Yb203 Ta2〇5 Bi203 W03 Te02 Zr02 4.403 4.403 2.903 2.903 2.903 2.903 2.903 2.903 AI2O3 Sb,〇3 0,012 0.012 0.01 2 0.012 0.012 0.012 0.012 0.012 Total 100.00 100.00 100.00 100,00 100.00 100.00 100.00 100.00 Ba+K 3.000 3.000 3.000 3.000 2.000 3.000 3.000 2.000 Nb+Ti 14.194 14.194 16.208 16.208 16.208 16.208 16.208 16.208 (Nb+Ba)/(Ti+Ca) 0.162 0.229 0.168 0.233 0.211 0.207 0.274 0.252 Ti/Nb 0.970 0.970 1.100 1.100 1.100 0.758 0.758 0.758 Li+Na+K+Cs 3.000 0.000 3.000 0.000 0.000 3.000 0.000 0.000 Mg+Ca+Sr+Ba+Zn 39.523 42,523 39.523 42.523 41.523 39.523 42.523 41.523 nd 1.7907 1.8111 1.7942 1.8148 1.8119 1.8044 1.8243 1.8213 Vd 33.3 33.2 32.2 32.1 32.0 31.7 31.6 31.6 9g, F 0.5882 0.5871 0.5918 0.5927 0.5919 0.5927 0.5932 0.5930 Wearing distance b (a=-0.00162) 0.64216 0.64094 0.64398 0.64476 0.64379 0.64411 0.64444 0.64420 Wear distance b (a=-0.00275) 0.67979 0.67845 0.68036 0.68103 0.67995 0.67993 0.68015 0.67991 λ8〇『ηηι1 430 442 442 452 441 443 451 449 λ7〇Γηηι1 392 399 399 404 399 400 403 400 Xsfnm'] 351 353 354 357 357 354 356 356 Test ( 2) Post-transmission rate / test (2) pre-transmission rate After test (2) λ70-test (2) before, 〇-35-163467.doc 201245078 [Table 2] Example 9 10 11 Si02 33.655 33.655 36.655 CaO 37.562 37.562 37.562 Nb205 8.718 8.718 8.718 Ti02 6.990 6.990 6.990 Li2〇Na20 K20 3.000 MgO SrO BaO 3.000 2.000 ZnO 1.961 1.961 1.961 B2O3 4.699 4.699 2.699 Y2O3 La2〇3 Gd2〇3 Yb2〇3 Τ^2〇5 Bi203 W03 Te02 Zr02 3.403 3.403 3.403 Al2〇3 Sb2〇3 0.012 0.012 0.012 Total 100.00 100.00 100.00 Ba +K 3.000 3.000 2.000 Nb+Ti 15.708 15.708 15.708 (Nb+Ba)/(Ti+Ca) 0.196 0.263 0.241 Ti/Nb 0.802 0.802 0.802 Li+Na+K+Cs 3.000 0.000 0.000 Mg+Ca+Sr+Ba+Zn 39.523 42.523 41.523 nd 1.8002 1.8216 1.8183 vd 32.1 31.9 31.9 0g, F 0.5923 0.5917 0.5929 Intercept b (a=-0.00162) 0.64439 0.64345 0.64466 Intercept b (a=-0.00275) 0.68066 0.67950 0.68071 λ80[ητη] 436 436 434 λ7〇 [ηηι] 396 397 396 λ5[ητη] 353 355 355 Test (II) Transmittance/Test (II) Front transmittance: 0.997 Test (II) After λ7〇-Test (2) Λγο 2.5 -36- 163467.doc 201245078 [Table 3] Example 12 13 14 15 16 17 18 19 Si02 30.655 30.655 33.655 30.655 33.655 33.655 33.655 33.655 CaO 37.562 37.562 37.562 37.562 37.562 37.562 40.562 34.562 Nb205 8.718 8.718 8.718 8.718 8.718 8.718 8.718 8.718 Ti02 6.990 6.990 6.990 6.990 6.990 6.990 6.990 6.990 Li20 Na2〇k2o 6.000 3.000 3.000 3.000 2.000 MgO SrO BaO 3.000 2.000 3.000 5.000 3.000 3.000 6.000 ZnO 1.961 1.961 1.961 1.961 1.961 1.961 1.961 1.961 B2O3 4.699 4.699 2.699 4.699 2.699 2.699 1.699 4.699 y2〇3 La2 〇3 Gd2〇3 Yb203 Ta2〇5 Bi203 W03 Te02 Zr02 3.403 3.403 3.403 3.403 3.403 3.403 3.403 Al2〇3 Sb2〇3 0.012 0.012 0,012 0.012 0.012 0.012 0.012 0.012 Total 100.00 100.00 100,00 100.00 100.00 100.00 100.00 100.00 Ba+K 6.000 6.000 5.000 6.000 5.000 5.000 3.000 6.000 Nb+Ti 15.708 15.708 15.708 15.708 15.708 15.708 15.708 15.708 (Nb+ Ba)/(Ti+Ca) 0.196 0.263 0.241 0.263 0.308 0.263 0.246 0.354 Ti/Nb 0.802 0.802 0.802 0.802 0.802 0.802 0.802 0.802 Li+Na+K+Cs 6.000 3.000 3.000 3.000 0.000 2.000 0.000 0.000 Mg+Ca+Sr+Ba+ Zn 39.523 42.523 41.523 42.523 44.523 42.523 45.523 42.523 n<i 1.7895 1.8088 1.8060 1.8083 1.8262 1.8118 1.8280 1.8213 Vd 32.3 32.1 32.1 32.2 32.0 32.1 32.0 32.0 eg,F 0.5900 0.5899 0.5893 0.5918 0.5920 0.5913 0.5918 0.5925 Wear distance b (a=-0.00162) 0.64234 0.64199 0.64134 0.64405 0.64386 0.64338 0.64373 0.64443 Wearing distance b (a=-0.00275) 0.67884 0.67826 0.67761 0.68044 0.68002 0.67965 0.67989 0.68059 λ8〇[ηηι] 430 441 441 437 440 440 440 443 λ7〇[ηΓπ] 393 397 397 396 398 397 398 399 Λ5[ηπι] 349 351 352 351 353 352 353 355 Test (2) Transmittance / Test (2) Front transmittance test (2) After 7 〇 _ Test (2) before λ7〇37- I63467.doc 201245078 [ Table 4] Practical example 20 21 22 23 24 25 26 27 Si02 33.655 33.655 33.655 30.655 27.655 30.655 30.655 30.655 CaO 34.562 37.562 37.562 37.562 3 7.562 34.562 34.562 37.562 Nb205 8.718 8.718 8.718 8.718 8.718 8.718 8.718 8.718 Ti02 6.990 6.990 6.990 6.990 6.990 6.990 6.990 6.990 Li20 Na20 K20 3.000 1.961 3.000 3.000 6.000 3.000 MgO SrO BaO 3.000 4.961 3.000 6.000 6.000 6.000 3.000 4.961 ZnO 1.961 1.961 1.961 1.961 1.961 B2O3 4.699 4.699 4.699 4.699 4.699 4.699 4.699 4.699 y2〇3 La2〇3 Gd2〇3 Yb203 Ta2〇5 Bi203 W03 Te02 Zr02 3.403 3.403 3.403 3.403 3.403 3.403 3.403 3.403 ai2〇3 Sbi〇3 0.012 0.012 0.012 0.012 0.012 0.012 0.012 0.012 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ba+K 6.000 4.961 4.961 6.000 9.000 9.000 9.000 7.961 Nb+Ti 15.708 15.708 15.708 15.708 15.708 15.708 15.708 15.708 (Nb+Ba)/(Ti+Ca) 0.282 0.307 0.263 0.330 0.330 0.354 0.282 0.307 Ti/Nb 0.802 0.802 0.802 0.802 0.802 0.802 0.802 0.802 Li+Na+K+Cs 3.000 0.000 1.961 0.000 3.000 3.000 6.000 3.000 Mg+C a+S r+B a+Zn 39.523 42.523 40.562 45.523 45.523 42.523 39.523 42.523 nd 1.8012 1.8181 1.8051 1.8284 1.8157 1.8095 1.7915 1.8067 vd 32.1 32.3 32.3 32.0 32.3 32.2 32.4 32.4 eg,F 0.5922 0.5922 0.5912 0.5902 0.5909 0.5905 0.5901 0.5913 Intercept b (a=- 0.00162) 0.64422 0.64460 0.64358 0.64210 0.64331 0.64269 0.64267 0.64380 Intercept b (a=-0.00275) 0.68050 0.68110 0.68008 0.67826 0.67981 0.67908 0.67928 0.68041 λ8〇[ιυηη] 437 440 436 443 443 446 428 434 λ7〇[ηηι] 397 397 395 400 396 399 392 394 λ5[ηπι] 352 354 353 353 348 351 348 350 Test (2) Transmittance / Test (2) Front transmittance test (2) After λ70 - Test (2) Before λ70 38 163467.doc 201245078 [Table 5] Example 28 29 30 31 32 33 34 35 Si02 30.655 27.655 30.655 30.655 30.655 30.655 30.655 30.655 CaO 37.562 37.562 37.562 37.562 34.562 34.562 37.562 37.562 Nb2〇5 8.718 8.718 8.718 8.718 8.718 8.718 8.718 8.718 Ti02 6.990 6.990 6.990 6.990 6.990 6.990 6.990 6.990 Li20 Na2〇K20 4.961 2.000 3.00 0 1.961 MgO SrO BaO 3.000 9.000 8.000 6.000 9.000 6.000 7.961 6.000 ZnO 1.961 1.961 1.961 1.961 1.961 B2O3 4.699 4.699 2.699 2.699 4.699 4.699 4.699 4.699 y2〇3 La2〇3 Gd2〇3 Yb203 Ta2〇5 Bi203 W〇3 Te02 Zr02 3.403 3.403 3.403 3.403 3.403 3.403 3.403 3.403 Al2〇3 Sb2〇3 0.012 0.012 0.012 0.012 0.012 0.012 0.012 0.012 Total 100.00 100,00 100.00 100.00 100.00 100.00 100.00 100.00 Ba+K 7.961 9.000 8.000 8.000 9.000 9.000 7.961 7.961 Nb+Ti 15.708 15.708 15.708 15.708 15.708 15.708 15.708 15.708 (Nb+Ba)/(Ti+Ca) 0.263 0.398 0.375 0.330 0.426 0.354 0.374 0.330 Ti/Nb 0.802 0.802 0.802 0.802 0.802 0.802 0.802 0.802 Li+Na+K+Cs 4.961 0.000 0.000 2.000 0.000 3.000 0.000 1.961 Mg+Ca +Sr+Ba+Zn 40.562 48.523 47.523 45.523 45.523 42.523 45.523 43.562 1.7948 1.8340 1.8325 1.8195 1.8283 1.8102 1.8247 1.8134 vd 32.5 32.2 32.1 32.2 32.2 32.2 32.4 32.4 9g, F 0.5892 0.5912 0.5915 0.59 13 0.5912 0.5908 0.5906 0.5902 Intercept b(a=-0.00162) 0.64185 0.64337 0.64351 0.64352 0.64339 0.64302 0.64315 0.64269 Intercept b(a=-0.00275) 0.67857 0.67976 0.67978 0.67991 0.67978 0.67940 0.67976 0.67930 λ8〇[ηηι] 430 448 448 447 454 447 450 445 λ70[ητη] 392 400 400 397 402 397 400 398 λ5[ητη] 348 351 352 350 353 351 353 351 Test (2) Transmittance / Test (2) Front transmittance test (2) After λ7〇-test (2) Before λ,. 39-163467.doc 201245078 . [Table 6] Example 36 37 38 39 40 41 42 Si02 30.655 30.655 30.655 30.655 30.655 30.655 30.655 CaO 37.562 37.562 37.562 37.562 35.562 35.562 35.562 Nb205 8.718 10.679 8.718 10.718 8.718 8.718 10.718 Ti02 6.990 6.990 6.990 6.990 6.990 6.990 6.990 U20 Na20 K20 3.000 3.000 3.000 3.000 3.000 3.000 3.000 MgO SrO BaO 3.000 3.000 3.000 3.000 3.000 3.000 3.000 ZnO 3.961 1.961 3.961 1.961 1.961 B2O3 4.699 4.699 2.699 2.699 4.699 4.699 4.699 Y2〇3 La2〇3 Gd2〇3 Yb203 T&2〇 5 Bi203 W03 Te02 Zr02 5.364 3.403 3.403 3.403 3.403 5.403 3.403 ai2〇3 Sb203 0.012 0.012 0.012 0.012 0.012 0.012 0.012 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ba+K 6.000 6.000 6.000 6.000 6.000 6.000 6.000 Nb+Ti 15.708 17.669 15.708 17.708 15.708 15.708 17.708 (Nb+Ba)/(Ti+Ca) 0.263 0.307 0.263 0.308 0,275 0.275 0.322 Ti/Nb 0.802 0.655 0.802 0.652 0.802 0.802 0 .652 Li+Na+K+Cs 3.000 3.000 3.000 3.000 3.000 3.000 3.000 Mg+Ca+Sr+Ba+Zn 40.562 40.562 44.523 42.523 42.523 40.523 40.523 n<i 1.8130 1.8270 1.8156 1.8344 1.8114 1.8167 1,8305 Vd 32.0 30.8 32.0 30.6 31 , 9 31.8 30.5 6g, F 0.5911 0.5941 0.5921 0.5943 0.5915 0.5923 0.5960 Load distance b (a=-0.00162) 0.64302 0.64402 0.64400 0.64393 0.64327 0.64389 0.64544 Intercept b (a=-0.00275) 0.67918 0.67882 0.68016 0.67851 0.67931 0.67983 0.67991 λ8〇[ηηι ] 435 452 440 459 442 444 454 λ7〇[ητη] 396 402 397 405 398 397 402 λ5[ηιη] 351 354 350 353 352 351 354 Test (2) Transmittance / Test (2) Front transmittance test (2) After λ7〇_ test (b) before λ7〇•40-163467.doc 201245078 [Table 7] Comparative Example ABCD Si02 28,468 14.434 5.333 9.228 CaO 30.203 24.922 29.998 28.246 Nb205 4.998 3.453 Ti02 11.431 11.012 19.050 19.825 Li20 3,804 Na20 1.630 K20 1.609 MgO 10.026 SrO 3.057 BaO 1.045 1.550 ZnO 8.163 5.907 B2O3 4.890 18.140 31.068 28.441 y2〇3 1.268 0.877 La2〇3 1.555 3.850 3.688 2.309 Gd〗 〇3 Yb203 T&2〇5 Bi2〇3 wo3 0.581 Te02 Zr02 4.582 5.261 3.901 2.571 ai2o3 5.700 3.884 Sb203 0,011 0.012 0.011 0.011 Total 100.00 100.00 100.00 100.00 Ba+K 0.000 1.609 1.045 1.550 Nb+ Ti 16.428 14.464 19.050 19.825 (Nb+Ba)/(Ti+Ca) 0.120 0.096 0.021 0.032 Ti/Nb 2.287 3.189 - - Li+Na+K+Cs 0.000 7.043 0.000 0.000 Mg+Ca+Sr+Ba+Zn 38.366 34.947 36.950 32.853 nd 1.8171 1.8061 1.8173 1.7884 Vd 32.1 34.2 32,6 33.2 eg,F 0.5944 0.5877 0.5950 0.5955 Intercept b(a=-0.00162) 0.64635 0.64309 0.64778 0.64924 Intercept b(a=-0.00275) 0.68263 0.68174 0.68462 0.68676 X8〇[nm ] 461 454 478 474 λ7〇[ηπι1 408 402 422 418 λ5[ΠΠ1] 359 349 363 363 Test (2) Transmittance / Test (2) Front transmittance 0.000 0.111 0.998 1.000 Test (2) After 7 〇 · Test (b) Pre-λ70 - - 1.0 2.0 •41 · 163467.doc 201245078 [Table 8] Example 43 44 45 46 47 48 49 Si02 36.655 36.655 36.655 33.655 33.655 33.655 33.655 CaO 37.562 37.562 3 7.562 37.562 37,562 37.562 40.562 Nb2〇5 7.718 7.204 7.204 7.204 7.204 7.204 7.204 Ti02 6.990 7.504 6.990 6.990 6.990 6.990 6.990 BaO Li2〇3.000 Na20 3.000 K20 MgO 3.000 SrO ZnO 1.961 1.961 1.961 1.961 1.961 1.961 1.961 B2O3 4.699 4.699 4.699 4.699 4.699 4.699 4.699 y2 〇3 LS2〇3 0.514 0.514 0.514 0.514 Gd2〇3 Yb203 Τ^2〇5 Bi2〇3 W03 Zr02 4.403 4.403 4.917 4.403 4.403 4.403 4.403 ai2〇3 Sb2〇3 0.012 0.012 0.012 0.012 0.012 0.012 0.012 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ba+K 0.000 0.000 0.000 0.000 0.000 0.000 0.000 Nb+Ti 14.708 14.708 14.194 14.194 14.194 14.194 14.194 (Nb+Ba)/(Ti+Ca) 0.173 0.160 0.162 0.162 0.162 0.162 0.151 Ti/Nb 0.906 1.042 0.970 0.970 0.970 0.970 0.970 Li +Na+K+Cs 0.000 0.000 0.000 3.000 3.000 0.000 0.000 Mg+Ca 十 Sr+Ba+Zn 39.523 39.523 39.523 39.523 39.523 42.523 42.523 n<i 1.8047 1.8024 1.8006 1.8102 1.7996 1.8099 1.8102 Vd 32.6 32.7 33.0 33.1 33.1 33.1 33.2 〇g, F 0.5905 0.5909 0.5909 0.5891 0.5889 0.5892 0.5890 Intercept b (a=*0.00162) 0.64333 0.64392 0.64439 0.64277 0.64261 0.64284 0.64281 Carrying distance b (a=>0.00275) 0.68017 0.68087 0.68168 0.68017 0.68002 0.68025 0.68033 λ8〇[ηηι] 428 422 431 434 431 440 434 λ7〇[ηηι] 392 391 394 395 393 397 395 λ5[ηηι] 355 355 354 352 351 354 353 Test (2) Transmittance / Test (2) Pre-transmission test (2) after λ70-test (2) before λ70 163467.doc -42-^ 201245078 [Table 9] Example 50 51 52 53 54 55 56 57 Si02 33.655 33.655 33.655 36.655 36.655 36.655 33.655 33.655 CaO 37.562 37.562 37.562 37.562 37.562 37.562 37.562 37.562 Nb205 7.204 7.204 7.204 7.718 8.718 9.218 10.204 7.204 Ti02 6.990 6.990 6.990 8.490 6,990 6.990 6.990 6.990 BaO Li20 Na2〇K20 MgO SrO 3.000 ZnO 1.961 4.961 1.961 1.961 1.961 1.961 1.961 1.961 B2O3 4.699 4.699 7.699 4.699 4.699 4.699 4.699 4.699 Y2〇3 L&2〇3 0.514 0.514 0.514 0.514 0.514 Gd203 Yb203 Ta2〇5 Bi2〇3 W03 3.000 Zr02 4.403 4.403 4.403 2.903 3.403 2.903 4.403 4.403 AI2O3 Sb203 0.012 0.012 0.012 0.012 0.012 0.012 0.012 0.012 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 Ba+ K 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 Nb+Ti 14.194 14.194 14.194 16.208 15.708 16.208 17.194 14.194 (Nb+Ba)/(Ti+Ca) 0.162 0.162 0.162 0.168 0,196 0.207 0.229 0.162 Ti/Nb 0.970 0.970 0.970 1.100 0.802 0.758 0.685 0.970 Li+Na+K+Cs 0.000 0.000 0.000 0.000 0.000 0.000 0.000 0.000 Mg+Ca+Sri-Ba+Zn 42.523 42.523 39.523 39.523 39.523 39.523 39.523 39.523 na 1.8096 1.8139 1.8018 1.8068 1.8114 1.8150 1.84166 1.82164 Vd 33.2 32.8 33.2 31.9 31.9 31.6 30.5 31.8 6g, F 0.5890 0.5895 0.5893 0.5934 0.5919 0.5945 0.5931 0.5916 Wearing distance b (a=-0.00162) 0.64279 0.64272 0.64309 0.64511 0.64366 0.64569 0.64259 0.64315 Carrying distance b (a=-0.00275) 0.68031 0.67979 0.68061 0.68115 0.679 71 0.68140 0.67706 0.67908 λβ〇[ηηι] 433 443 436 463 445 450 440 440 λ7〇[ητη] 396 399 397 406 400 403 398 398 λ5[ηπι] 353 354 354 358 357 357 357 357 Test (2) Transmittance / Test (b) pre-transmission rate 0.996 0.999 test (2) after λ7 〇-test (b) before λ70 2.5 1.5 as shown in Table 1 to Table 9, part of the vd$ in the optical glass of the embodiment of the present invention The dispersion ratio (0g, F) is (-0.00275xvd+0.68125) or less, -43-163467.doc 201245078 is more detailed and S is (_0.00275xvd+0.67991) or less. Also, vd>31. The P-part dispersion ratio (Gg, F) is (_0 0 〇 162 x vd + 〇 64622) or less, and is more detailed, and is (-〇.〇〇162xvd+〇 64476). On the other hand, the partial dispersion ratio (0g, F) of the optical glass of the embodiment of the present invention is (_〇 〇〇 162xvd + 638.63822) or more ‘more specifically, it is (-0.00162xvd+0.64094) or more. That is, the relationship between the partial dispersion ratio (eg, F) and the Abbe number (Vd) of the glass of the embodiment of the present application is as shown in Fig. 2 (first optical glass) and Fig. 3 (second optical glass). Therefore, it is known that the partial dispersion ratio (eg, f) is within the expected range. On the other hand, the glass of the comparative example (N〇 A to No. D) of the present invention is

Vd > 31 ' and the partial dispersion ratio (eg, F) exceeds (-0.00i62xvd + 0.64622). Therefore, it has been found that the optical glass of the embodiment of the present invention has a smaller partial dispersion ratio (0 匕 F) in the relational expression with the Abbe number (Vd) than the glass of the comparative example. Further, the refractive index (nd) of the optical glass of the embodiment of the present invention is 丨7〇 or more, more specifically 1.78 or more, and at the same time, the refractive index (nd) is 2.20 or less, and more specifically 185. Below, it is within the desired range. Further, the Abbe number (Vd) of the optical glass of the embodiment of the present invention is 2 Å or more, and more specifically 30 or more, and at the same time, the Abbe number (v < j) is 4 Å or less'. In the case of 34 or less, it is within the desired range. On the other hand, the glass of Comparative Example (No. B) of the present invention has a Vd exceeding 34. Therefore, it is understood that the optical glass of the embodiment of the present invention has a smaller Abbe number (vd) than the glass of Comparative Example (N〇B). Moreover, the transmittance of the test piece td line of the test piece of the optical glass used in the reheating test of the optical glass of the embodiment of the present invention (2) is divided by the transmittance of the d line of the test piece before the reheating test. The values are all above 95, more specifically Ο." above, within the desired range. &, the transmittance of the test piece before and after the reheating test (2) of the optical glass of the embodiment of the present invention The difference is 2 〇 nm or less, more specifically 〖5 nm or less, within a desired range. On the other hand, the glass of the comparative example (N〇A, N〇B) of the present invention is reheated. (2) The transmittance of the d-line of the subsequent test piece divided by the transmittance of the d-line of the test piece before the reheating test is less than 9595, after the reheating test (2), relative to visible light The transmittance of all the wavelengths was less than 70%. Therefore, it was found that the optical glass of the embodiment of the present invention is less likely to cause coloring or loss due to reheating than the glass of the comparative example (No. A, No. B). Further, the kQ of the optical glass of the embodiment of the present invention (the transmittance is 7〇%) The lengths are all below 500 nm, more specifically 407 nm or less. Further, the wavelength of λ 〆 transmittance of the optical glass of the embodiment of the present invention is 420 nm or less, and more specifically 359. Further, the λ8 光学 (wavelength at a transmittance of 80°/.) of the optical glass of the embodiment of the present invention is 560 nm or less, and is 463 nm or less in more detail. Therefore, the present invention is known. The optical glass of the embodiment has a high transmittance with respect to visible light and is not easily colored. Therefore, it is known that the refractive index (...) and the Abbe number (vd) of the optical glass of the embodiment of the present invention are within a desired range. Further, the transmittance is higher with respect to visible light, and the chromatic aberration is small, and the extrusion property is high. The present invention has been described in detail above for the purpose of illustration, but it is understood that the present embodiment is The purpose is only for the sake of illustration, and various practitioners can apply many changes without departing from the idea and scope of the invention of 163467.doc -45-201245078. [Simplified illustration] Figure 1 shows the partial dispersion ratio 0g, F) The vertical axis and the Abbe number (Vd) are the horizontal axis Fig. 2 is a view showing the relationship between the partial dispersion ratio (Gg, F) and the Abbe number (vd) in the embodiment of the first optical glass of the present application. 3 is a diagram showing the relationship between the partial dispersion ratio (0g, F) and the Abbe number (Vd) of the embodiment of the second optical glass of the present application. 163467.doc 46

Claims (1)

201245078 VII. Patent application scope: 1. An optical glass which is based on the total mass of the glass in terms of oxide conversion, containing 20.0% or more and 60.0% or less of the SiO2 component and more than 20.0% of the CaO component. And 50.0% or less, the content of the Nb205 component is 30.0% or less 'between the partial dispersion ratio (0g, F) and the Abbe number (vd) in the range of vd$31 (-〇.〇〇l62>< Vd+〇.63822)s(0g F) $ (-0.00275 xvd+0.68 125), which satisfies (-0.00162xvd+0.63822)$(eg,F)S(-〇.〇 in the range of vd>3 1 〇i62xvd+0.64622) relationship. 2. The optical glass of claim 1, wherein the sum of the contents of the BaO component and the K2 bismuth component is more than 〇% and 20.0% or less with respect to the total mass of the glass of the oxide-converted composition. 3. The optical glass according to claim 1, wherein the total mass of the glass relative to the oxide-converted composition is 〇% to 2% 〇% in terms of mol%. 4. The optical glass of the claim ,, wherein the total mass of the glass relative to the oxide-converted composition contains, in % by mole, a Ti〇2 component 〇~1〇〇〇/. . 5. The optical glass of the claim ,, wherein the sum of the contents of the NhO5 component and the Ti〇2 component is 10.0% or more and 40.0% or less with respect to the total mass of the glass of the oxide conversion composition. 6. The optical glass of claim 1, wherein the mass of the glass relative to the composition of the oxide is 5% to 25% by weight based on the mole % of the Ba. 7. The optical glass of claim 1, wherein the total mass of the glass converted to the oxide is 含有% to 2% by mass based on the mole %. 8. The optical glass of the request, wherein the molar ratio of the molar ratio is 163467.doc 201245078 (Nb2〇5+Ba〇)/(Ti02+CaO) is 0.100 or more. 9. The optical glass of the requester has an oxide conversion composition ratio of Ti 〇 2 / Nb 2 〇 5 of 5 〇〇 or less. A. For example, the optical glass of the requester, wherein the oxide conversion composition of the molar ratio of 1 〇 2 / 灿 2 〇 5 is less than 3 。. U. The optical glass of claim 1, wherein the mass of the glass relative to the composition of the oxide is in terms of mol%, Li2〇 composition 〇~25·〇% and/or Na2〇 composition 〇~25.0% and/or Or κ2〇 composition 〇~25.0% and/or Cs2〇 composition 〇~1〇.〇〇/0. 12. For the optical glass of the request item, the glass of her material is the total mass of the glass composed of oxides, and the RkO component (formula K, T & is selected from the group consisting of Li, Na, K, Cs). In the group, the above species are 11 L咕+, ) Wuer and 30.0〇/〇 below 〇13·If the optical glass of the request item is ,, the glass Μ哲县Mohr%, Mg〇 component 0~20.0% and/or Sr〇 component 0~20.0°/. And / or ZnO composition 〇 ~ 30 〇〇 /. . 14. The optical glass of the claim ,, wherein the glass total mass 'RO component (formula: p-diox: (tetra) &, Ba, Zn is selected from the group consisting of lea and above 60. The above is the temperature of 20·0°/〇15. The optical glass of claim 1 is composed of I63467.doc 201245078. The total mass of the glass, in mol%, P205 composition 〇~30.0 % and / or B2O3 components 〇 ~ 40.0% and / or Ge02 components 0 - 20.0% and / or • Υ 2 〇 3 components 0 ~ 15.0% and / or • La2 〇 3 components 〇 ~ 15.0% and / or Gd203 components 0 ~ 15.0% and/or Yb203 component 0~15.0% and/or Ta2〇5 component 〇~15.0% and/or Bi2〇3 component 0~15.0% and/or W03 component 〇~20.0% and/or Te02 component 〇~30.0 % and/or Zr〇2 component 0~15.0% and/or a12〇3 component 0~15.0% and/or Sb2〇3 component 0~1.0% » 16. As claimed in the optical glass, it has 17〇 or more A refractive index (nd) of 22 Å or less and an Abbe number (vd) of 20 or more and 40 or less. For example, the optical glass of item 1 wherein the wavelength of the spectral transmittance is displayed (λ7°) is 5 〇〇 nm or less. • The optical glass of claim 1, wherein the transmittance of the light at the wavelength of 587.56 nm (d line) of the ° test piece after the reheat test (2) described below is divided by the test piece before the above reheat test. The value obtained by the transmittance of the line is 0.95 or more. [Reheating test (2): The test piece is heated at 15 mm x 15 mm>< 30 mm and then 163467.doc 201245078, and the temperature is raised from room temperature for 1 to 50 minutes to each sample. The temperature at which the transfer temperature (Tg) is 80 ° C higher is 80 higher than the glass transition temperature (Tg) of the above optical glass. The mixture was kept at a temperature of 30 minutes, and then naturally cooled to room temperature. The opposite sides of the test piece were ground to a thickness of mm, and visual observation was carried out. 19. The optical glass of claim 1, wherein the transmittance of the test piece before the reheating test (2) is 70% of the wavelength, that is, the difference between the λ7 〇 and the person after the reheating test. 20 ππι or less, [reheat test (2). Test piece 1 5 mm x 15 mm>< 30 mm reheating 'temperature rise from room temperature for 150 minutes to 80 ° C higher than the transfer temperature (Tg) of each sample The temperature 'in the above-mentioned glass of the optical glass is transferred to the south of the optical glass (Tg) for 30 minutes at a temperature of 3, and then naturally cooled to normal temperature, and the opposite sides of the test piece are ground to a thickness of 1 〇. After mm, visual observation] 20. A preform for grinding and/or precision extrusion comprising the optical glass of any one of claims 1 to 19. 21. , which is obtained by grinding and/or grinding the optical glass of any one of the items 19 to 22. 22. An optical element which is precisely extruded as claimed in any one of claims 1 to 19. Optical glass" -4- 163467.doc S