TW201249769A - Optical glass, preform and optical element - Google Patents

Abstract

Provided are: an optical glass which has improved transparency with respect to visible light and has small Abbe number (vd) and low partial dispersion ratio (θg, F), while having a refractive index (nd) within a desired range; a preform using the optical glass; and an optical element using the optical glass. This optical glass contains, in mol% relative to the total amount of glass components in the composition in terms of oxides, 10.0-60.0% (inclusive) of an SiO2 component, more than 0% but 25.0% or less of a BaO component, more than 0% but 15.0% or less of an La2O3 component, and more than 0% but 20.0% or less of an Nb2O5 component. The partial dispersion ratio (θg, F) and the Abbe number (vd) of this optical glass satisfy (-0.00162 vd + 0.63822) = (θg, F) = (-0.00275 vd + 0.68125) within the range of vd = 31, while satisfying (-0.00162 vd + 0.63822) = (θg, F) = (-0.00162 vd + 0.64622) within the range of vd > 31.

Description

201249769 VI. Description of the Invention: TECHNICAL FIELD 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, but 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 that takes into account the motion 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, the partial dispersion ratio (eg, 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 (eg, 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 the optical glass 'partial dispersion ratio (4) indicating partial dispersion in the short wavelength region, F) and Abbe number (5) There is a general linear relationship between them. The straight line indicating the relationship is based on the partial dispersion ratio of the vertical axis, F), and the orthogonal coordinates of the Abbe number (vd) on the horizontal axis to connect and depict the partial dispersion ratio of the PMA2 and the 163468.doc 201249769 PBM2. A straight line of 2 points of the number of shells is called a regular line (refer to Figure 1). The standard glass that becomes the basis for the regular line varies according to each optical glass manufacturer, but each company defines it with approximately 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 (eg, F) is 0.5436. Here, 'as a glass having high dispersion', for example, optical glasses as disclosed in Patent Documents 1 to 3 are known. [Prior Art Document] [Patent Document 1] Japanese Patent Laid-Open Publication No. 2009-179522 [Patent Document 2] Japanese Patent Laid-Open Publication No. 2009-2031, No. 34 [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, and it is not sufficient for the lens used for correcting the above secondary spectrum. Further, in the glass 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. Namely, an optical glass having a small Abbe number (vd) and a high dispersion, a small partial dispersion ratio (0g, 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 folding 163468.doc 201249769, the radiance (nd) is within a desired range, and the Abbe number (Vd) is small, and the partial dispersion ratio (eg 'f) An optical glass having a small transparency and improved transparency with respect to visible light, and a preform and an optical element using the optical glass. [Means for Solving the Problems] The present inventors have conducted intensive experimental research to solve the above problems, and as a result, it has been found that the BaO component, the La203 component, and the Nb205 component are used in combination, and the contents are set within a specific range. The present invention is finally accomplished by having a desired relationship between the partial dispersion ratio (eg 'F) of the glass and the Abbe number (vd). At the same time, it has been found that the high refractive index of the glass can be achieved by using the La203 component and the Nb205 component in combination and setting the content within a specific range. Further, it has been found that by using the SiO 2 component, the BaO component and the La 203 component in combination, and the content thereof is set within a specific range, the stability of the glass can be improved, and the color of the glass can be reduced. Further, it has been found that by using the SiO 2 component, the BaO component, the La 203 component, and the Nb 2 〇 5 component in combination, and the content thereof is set within a specific range, coloring or devitrification is less likely to occur when the glass is reheated. In particular, the present invention provides the following. (1) An optical glass containing 1% by mass or more and 60.0% or less of the SiO 2 component, and more than 〇% and 25.0% of the BaO component, and the La203 component, in terms of the total mass of the glass of the oxide-converted composition. More than 〇% and 15.0% or less, and Nb2〇5 components are more than 0% and 20.0% or less, between the partial dispersion ratio (eg, F) and the Abbe number (vd), in the range of vd $ 3 1 Satisfy the relationship of 163468.doc 201249769 (-0.00162xvd+0.63822)^(9g . F)^ (.〇.〇〇275xvd+0.68 125), which satisfies in the range of vd>31 (_〇.〇〇i62xvd+0.63822 ) < (9g, F) S (-0.00162xvd + 0.64622) relationship. (2) The optical glass of (1), wherein the total mass of the glass relative to the oxide-converted composition is more than 〇% and less than 2% by weight of the Ba0 component, and the Nb205 component is more than 〇. % and less than 19 5〇/〇. (3) The optical glass of (1) or (2), wherein the content of the Li" component is 3 〇.% or less based on the total mass of the glass of the oxide-converted composition. (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 more than 0% and 30.0% in terms of % by mole of U2〇 the following. (5) The optical glass according to any one of (1) to (4), wherein the content of the Ti〇2 component is less than 20.0% in terms of mol% relative to the total mass of the glass in terms of oxide composition. (6) The optical glass according to any one of (1) to (5), wherein the content of the Ti〇2 component is 17.5% or less in terms of mol% of the total glass composition of the oxide-converted composition. (7) The optical glass according to any one of (1) to (6), wherein the molar ratio (Ba〇+La203)/(Nb205+Ti02) of the oxide conversion composition is 〇.〇5 or more. (8) The optical glass according to any one of (1) to (7), wherein the molar ratio of the molar ratio Ti02/Nb205 is 5.0 or less. (9) The optical glass of any one of (1) to (8), wherein the mass of the glass relative to the composition of the oxide is in the range of mol/. The content of B2〇3 is 163,468.doc 201249769 The amount is 40.0% or less. (10) The optical glass according to any one of (1) to (9), wherein the content of the B2〇3 component is 20.0% or less based on the total mass of the glass in terms of the oxide conversion composition. (11) The optical glass according to any one of (1) to (10), wherein the oxide conversion composition has a molar ratio of Nb205/(Si02+B2〇3) of 0.070 or more. (12) The optical glass of any one of (1) to (11), wherein the total mass of the glass relative to the composition of the oxide is expressed in mol%,

The MgO component 〇 is 20.0% and/or the CaO component is 0 to 20.0% and/or the SrO component is 〇 20.0% and/or the ZnO component is 〇 30.0%. (13) The optical glass according to any one of (1) to (12), wherein, in relation to the total mass of the glass of the oxide-converted composition, the R〇 component (wherein R is selected from the group consisting of Mg, Ca, Sr, The molar ratio of one or more of the group consisting of Ba and Zn is 35.0% or less. (14) The optical glass according to any one of (1) to (13), wherein the molar ratio of the molar composition is Ba0/R0 (wherein the ruler is selected from the group consisting of Mg, ^, ^, Ba, Zn) Among the group of groups, the above species are more than 2〇. (15) The optical glass of any one of (1) to (14), wherein the total mass of the glass relative to the composition of the oxide is expressed in mol%,

Na20 component 〇~25.0% and/or K2〇 component 0~25.0% and/or Cs2〇 component 〇~lo o. /. . </ RTI> </ RTI> </ RTI> </ RTI> </ RTI> </ RTI> <RTIgt; </ RTI> <RTIgt; </ RTI> <RTIgt; </ RTI> <RTIgt; </ RTI> <RTIgt; The molar ratio of one or more of the groups consisting of K and Cs is 30.0% or less. (17) The optical glass according to any one of (1) to (16), wherein the total mass of the glass relative to the oxide-converted composition is in terms of mol%, P2O5 component 〇~30.0% and/or Ge02 component 〇20.0% and/or Y2〇3 component 〇15.0% and/or Gd203 component 0~15.0% and/or Yb203 component 0~15.0% and/or Ta205 component 0~15.0% and/or Bi2〇3 component〇 ~15.0% and/or W〇3 component 0~20.0% and/or Te02 component 0~30.0% and/or Zr02 component 0~15.0% and/or Al2〇3 component 0~15.0% and/or Sb2〇3 component 〇~1.0%. (18) The optical glass according to any one of (1) to (17), wherein the molar ratio of the oxide conversion composition (B203/SiO2) is 1.00 or less. (19) The optical glass according to any one of (1) to (18) which has a refractive index (nd)' of 1.97〇 or more and 1.95 or less and an Abbe's number (vd) of 20 or more and 40 or less. (20) The optical glass according to any one of (1) to (19), wherein the spectroscopic transmission 163468.doc 201249769 rate shows that 70% of the wavelength (λ7〇) is 500 nm or less. (21) The optical glass of any one of (1) to (2), wherein the transmittance of the light having a wavelength of 587.56 nm (d line) of the test piece after the reheating test (2) is divided by the above The value obtained by the transmittance of the d-line of the test piece before the heating test was 0.95 or more, [reheating test (2): reheating the test piece 15 mm x 15 mm&gt;&lt; 30 mm, and heating up to room temperature for 5 minutes from room temperature The temperature is 80 ° C higher than the transfer temperature (Tg) of each sample, and the temperature is maintained at a temperature 80 ° C higher than the glass transition temperature (Tg) of the optical glass for 30 minutes, and then naturally cooled to normal temperature, and the test is performed. After the two sides of the sheet were ground to a thickness of 10 mm, visual observation was performed]. (22) The optical glass of any one of (1) to (21), wherein the transmittance of the test piece before the reheating test (II) is 70°/. The difference between the wavelength λ7〇 and the λ7〇 of the test piece after the above reheating test is 20 nm or less, [reheating test (2): reheating the test piece 15 mmM5 mmx30 mm, and heating up from room temperature for 150 minutes The transfer temperature (Tg) of each sample is higher than 80, and the temperature is maintained at a temperature 80 ° C higher than the glass transition temperature (Tg) of the optical glass for 3 minutes, and then naturally cooled to normal temperature. The two surfaces were ground to a thickness of 1 〇 mm, and visual observation was performed. (23) A preform for polishing processing and/or precision extrusion molding, comprising the optical glass of any one of (1) to (22) + any one. (24) An optical element obtained by grinding and/or grinding an optical glass according to any one of (1) to (22). 163468.doc 201249769 (25) An optical element which is formed by precision extrusion of an optical glass of any one of (丨) to (22). [Effects of the Invention] According to the present invention, by using the SiO 2 component, the BaO component, the La 203 component, and the Nb 2 〇 5 component in combination, and setting the contents in a specific range, the refractive index and the high dispersion of the glass can be achieved. And the glass portion can be dispersed to have a desired relationship between Mg 'F) and Abbe number (Vd), and the color of the glass is reduced. Therefore, an optical glass having a refractive index (nd) and an Abbe number (Vd) in a desired range and having a small chromatic aberration and high transparency with respect to visible light, and a preform using the optical glass can be obtained. Body and optical components. [Embodiment] The optical glass of the present invention contains 1% by mass or more and 60.0% or less of the Si〇2 component, and more than 〇% of the BaO component with respect to the total mass of the glass of the oxide-converted composition. % or less, the La203 component is more than 〇% and 15.0% or less, and the Nt&gt;2〇5 component is more than 〇% and 20.0% or less, and is between the partial dispersion ratio (0g 'F) and the Abbe number (Vd). The relationship satisfying (-0.00162xvd+0.63822)^(0g · F)^ (-0.00275xvd+0.68125) in the range of vd$31 satisfies in the range of vd&gt;3 1 (_〇〇〇i62xvd+〇.63822) The relationship between S (eg ' F ) $ (-〇.〇〇l62xvd+0.64622). By using the La2〇3 component and the Nb&gt;2〇5 component in combination, and setting the content to a specific range, the high refractive index of the glass can be achieved. At the same time, by using Nb2〇5 component and setting the content within a specific range, high dispersion of glass (low Abbe number) can be achieved. At the same time, by using the Ba〇 component, [seven... into 163468.doc •10·201249769 knife and Nt&gt; 2〇5 into a knife, and setting the content within a specific range, the glass part can be made. There is a desirable relationship between the dispersion ratio (eg, F) and the Abbe number (%). At the same time, by using the Si〇2 component, the Ba〇 component, and the La203 component in combination, and setting the content in a specific range, the stability of the glass can be improved, and the coloring of the glass can be reduced by β. An optical glass having a refractive index within a desired range, a small Abbe number (6), a small partial dispersion ratio (eg, f), and high transparency with respect to visible light, and a preform using the optical glass And optical components. On the other hand, by using the si〇2 component, the Ba0 component, the La2〇3 component, and the Nb2〇s component in combination, and setting the content 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 (0g, F) is small, the transparency with respect to visible light is high, and A high-extrudability optical glass, and a preform and an optical element using the optical glass. The optical glass of the present invention may also be in the form of a molar mass of the glass in terms of oxide composition. /❶, the content of the BaO component is set to 20·〇❶/. Hereinafter, the content of the Nb205 component is set to be less than 19.5%. 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. 163468.doc 201249769 In the present specification, the content of each component is expressed by the % of the total mass of the glass in terms of the composition of the oxide, unless otherwise specified. Here, the "oxide-converting composition" is a composition in which an oxide, a composite salt, and a metal fluoride which are assumed to be used as a raw material of the glass constituent component of the present invention are equal to when they are all decomposed and become oxides during melting. The total mass of the produced oxide was set to 1% by mole, and each component contained in the glass was expressed. <About essential ingredients, arbitrary ingredients>

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 10.0% or more, it is possible to obtain a glass excellent in devitrification resistance without greatly increasing the partial dispersion ratio of the glass. Further, by this, devitrification or coloration at the time of reheating can be reduced. Further, by setting the content of the 3丨02 component to 60.0% or less, the refractive index of the glass is not easily lowered, whereby the glass portion can be suppressed and the glass portion can be suppressed.

K2SiF6, Na2SiF6, etc. are used as raw materials. It is easy to obtain the desired higher refractive index and increase the dispersion ratio. Again, by Chiang a

And the composition of the glass is resistant to devitrification. Reduce the dispersion of the glass. Especially by containing BaO into 163468.doc •12.201249769::: quantity more than 0%', it is easy to obtain a glass with high devitrification resistance and achieve a desired higher refractive index and a lower partial dispersion ratio. . Moreover, by this, devitrification or coloring at the time of reheating can be reduced. On the other hand, by setting the content of the Ba〇 component to 25 % by weight or less, it is more preferable to suppress the deterioration of the devitrification resistance or the chemical durability caused by the excessive content of the BaO component. Therefore, the lower limit of the content of the total amount of the glass relative to the oxide-converted composition is preferably more than 〇%, more preferably 1 genius, and most preferably 3. G%. Further, the upper limit of the content of the Ba 〇 component is preferably 25.0%, more preferably 2 〇.〇%, still more preferably 15 is preferably 1 〇.〇%. As the BaO component, BaC〇3, Ba(N〇3)2 or the like can be used as a raw material.

The LazOs component increases the refractive index of the glass and lowers the composition of the partial dispersion ratio. In particular, by containing more than 〇% of the La2〇3 component, it is easy to obtain a glass having high devitrification resistance, and a desired higher refractive index and a lower partial dispersion ratio can be achieved. On the other hand, by setting the content of the bismuth component to 15.0% or less, the devitrification of the glass containing the excessive amount of the La2〇3 component can be reduced, and the increase in the Abbe number of the glass can be suppressed. The lower limit of the content of the La2〇3 component is preferably set to more than 〇%, more preferably i, still more preferably 1.5%, most preferably 3.0%, relative to the total mass of the glass of the oxide-converted composition. The upper limit of the content of the La2〇3 component is preferably set to 15.0%, more preferably 12.0%, and most preferably 1% by weight. La2〇3, La(N〇3)rXH2〇 can be used for the La2〇3 component. (X is an arbitrary integer) and the like as a raw material.

The Nb&gt;2〇5 component increases the refractive index of the glass, lowers the Abbe number, and lowers the composition of the partial dispersion ratio. In particular, by containing more than 163468.doc •13·201249769 〇%' of the Nb2〇5 component, the refractive index of the glass can be increased, the Abbe number can be lowered, and the partial dispersion ratio of the glass can be lowered. In addition, the content of the WNb2〇5 component is set to 2% or less, and it is more preferable that I is 19.5%. [彳Inhibition & increase in the brightness of the glass during the manufacture of the glass. The lower limit of the content of the total mass, the content of the Nb2〇5 component is preferably set to be more than 〇%, more preferably 1.0%, and most preferably 3.5%. Further, the upper limit of the content of the scented 〇5 〇5 component is preferably set. It is 20.0%, more preferably less than 195%, more preferably 17%, and most preferably 16.0%. Nb2〇5 can be used as a raw material.

The LhO component is an optional component in the optical glass of the present invention which improves the meltability of the glass and lowers the partial dispersion ratio of the glass. In particular, by setting the content of the LhO component to 30.% or less, it is easy to achieve a high refractive index, and at the same time, it is possible to reduce the whitening or the formation of the glass caused by the excessive content of the LhO component or during reheating. Crystallization precipitates to improve the chemical durability of the glass. Therefore, the upper limit of the content of the LhO component is preferably set to 3% by mole, more preferably 27.0%, still more preferably 25.0%, and most preferably 2% by weight based on the total mass of the glass of the oxide-converted composition. . Further, the optical glass of the present invention may not contain the LhO component from the viewpoint of improving the extrusion formability, but may lower the glass transition point (Tg), lower the partial dispersion ratio, and reduce devitrification upon reheating or From the viewpoint of coloring, the lower limit of the content of the Li 2 〇 component relative to the total mass of the glass oxide composition is preferably set to more than 〇%, more preferably, more preferably 3 〇% 〇 Li2 〇 As the raw material, Li2C03, LiN03, LiF or the like can be used as a raw material.

The Ti 2 component is a component which increases the refractive index of the glass and lowers the Abbe number and is an arbitrary component in the optical glass of the present invention. In particular, the content of the composition of Ti〇2 I63468.doc 201249769 is set to be less than 20·0%', more preferably π.5°/. Hereinafter, the coloring of the glass can be reduced to increase the internal transmittance of the glass. Further, the content of the Ti 2 component was set to be less than 20.0 ° /. More preferably, it is 17.5% or less, and the partial dispersion ratio is not easily increased, so that a lower partial dispersion ratio close to the regular line can be easily obtained. Therefore, the upper limit of the content of the Τι〇2 component is preferably set to less than 2 〇%, more preferably 18.0, based on the total amount of the glass of the oxide-converted composition. /. Further, it is preferably 17.5%, more preferably less than 15%, and even more preferably 13.0%, and most preferably 10.0%. On the other hand, from the viewpoint of reducing coloring, it is preferred that the Ti〇2 component is not contained, but the content of the Ti〇2 component is obtained from the viewpoint of obtaining a higher refractive index and improving resistance to devitrification. The lower limit is preferably set to be more than 〇%', more preferably 〇·1%, still more preferably 1.0%, and most preferably 3.0%. As the Ti〇2 component, Ti〇2 or the like can be used as a raw material. In the optical glass of the present invention, the ratio of the sum of the content of the Ba0 component and the La2〇3 component to the sum of the contents of the Nb2〇5 component and the Ti〇2 component is preferably 〇5 or more. Thereby, the refractive index is increased, and the partial dispersion ratio becomes low, so that a desired higher refractive index can be obtained, and a lower partial dispersion ratio can be obtained. Therefore, the lower limit of the molar ratio (Ba〇+La2〇3)/(NhOdTiO2) of the oxide-converted composition is preferably set to 〇〇5, more preferably 〇ι〇, still more preferably 0.20, and most preferably 〇.30. On the other hand, the upper limit of the molar ratio (BaO+I^O^WhOdTiO2) is not particularly limited, and is, for example, 5.00 or more, more specifically 3 Å or less, and more specifically 1 00. the following. Further, the optical glass of the present invention preferably has a molar ratio of Ti〇2/Nb2〇5 of 5.5% or less in terms of oxide composition. Thereby, the Abbe number of the glass can be adjusted within the range desired by 163468.doc 15 201249769, 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. Further, by this, an optical glass having less coloration can be obtained. Therefore, the upper limit of the molar ratio Ti〇2/Nb2〇5 of the oxide-converted composition is preferably 5 〇, more preferably 4.5, and still more preferably 4.3 ^ especially for the Ba 〇 component and the La 2 〇 3 component. In the optical glass of the invention of the present application which is an essential component, the Ti〇2/Nb2〇5 is preferably 25 or less from the viewpoint of further reducing the partial dispersion ratio. The B2〇3 component is a component which promotes stable glass formation, improves devitrification resistance, and improves the meltability of glass, and is an arbitrary component in the optical glass of the present invention. In particular, the content of the B2〇3 component is 40.0% or less, more preferably 20.0°/. In the following, a desired higher refractive index can be obtained, and at the same time, an increase in the partial dispersion ratio of the glass can be suppressed. Further, by this, it is possible to reduce the devitrification at the time of reheating of the glass. Therefore, the upper limit of the content of the glass total mass 'B2〇3 component with respect to the oxide-converted composition is preferably set to 4% by weight, more preferably It is 30.0%', more preferably 20.0%, still more preferably 18%, and even more preferably 15.0. /. 'Best is ι〇·0%. As the raw material of b2〇3, h3b〇3, Na2B407, Na2B407.l〇H20, BP04 or the like can be used. The optical glass of the present invention preferably has a ratio of the content of the Nb2〇5 component to the sum of the contents of the Si〇2 component and the Βζ〇3 component of 〇 7〇 or more. Thereby, the refractive index is increased 'and the partial dispersion ratio becomes low, so that a glass having a refractive index within a desired range and having a relatively small partial dispersion can be obtained. Therefore, the lower limit of the molar ratio Nb205/(si02+B203) of the oxide-converted composition is preferably set to 0.070, more preferably 0.091, and still more preferably 〇13〇β, on the other hand, the molar ratio Nb2〇5 The upper limit of /(Si〇2+B2〇3) is not particularly limited, and the optical glass of the invention 163468.doc '16 - 201249769 has a molar ratio of Nb2〇5/(Si〇2+B2〇3) of about 1 〇〇〇 The following 'more details are 0.700 or less, and more specifically 〇5〇〇 or less.

The MgO component is a component which lowers the melting temperature of the glass and is an optional component in the light dry glass of the present invention. In particular, by setting the content of the MgO component to 20.0% or less, a desired high refractive index can be obtained, and the devitrification property of the glass 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 20.0%, more preferably 10 _0%, and most preferably 5.0%, based on the total mass of the glass of the oxide-converted composition. As the MgO component, Mg0, MgC3, MgF2 or the like can be used as a raw material.

The CaO component is a component which lowers the devitrification 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 Ca 〇 component to 20.0% or less, a desired high refractive index can be obtained, and deterioration of chemical durability of the glass can be suppressed. Further, by this, devitrification or coloration at the time of reheating can be reduced. Therefore, the upper limit of the content of the CaO component is preferably set to 2% by weight, more preferably (7)%, more preferably 6.5%, and most preferably 5 〇0, based on the total mass of the glass of the oxide-converted composition. /〇. As the Ca 〇 component, CaC 〇 3, CaF 2 or the like can be used as a raw material.

The SrO component is a component which increases the refractive index of the glass and improves the resistance to devitrification of the glass, and is an optional component in the optical glass of the present invention. In particular, by setting the content of SrO to 2 〇% or less, deterioration of chemical durability of the glass can be suppressed. Therefore, the upper limit of the content of the δ Γ〇 component is preferably set to 20.0%, more preferably 15.0%, and 163468.doc 201249769 is preferably 10_0 with respect to the total mass of the glass of the oxide-converted composition. /〇. As the SrO component, Sr(N〇3)2, SrF2 or the like can be used as a raw material. ,

The ZnO component improves the resistance to devitrification 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 ZnO component to 3 〇% or less, the devitrification of the glass during reheating can be reduced, and the chemical durability of the glass can be improved. Further, by this, devitrification or coloration at the time of reheating can be reduced. Therefore, the upper limit of the content of the ZnO component is preferably set to 30.0%, more preferably 20.0%, still more preferably 13.0%, and still more preferably 12.0%, based on the total mass of the glass of the oxide-converted composition. It is 10·0%. In particular, the content of the ZnO component may be set to ι.〇% or less from the viewpoint of improving resistance to devitrification. As the raw material, ZnO, ZnF2 or the like can be used as the Ζη〇 component. In the optical glass of the present invention, the RO component (wherein 'R is selected from the group consisting of Zn, Mg, Ca, Sr, and Ba) is used to improve the devitrification resistance of the glass, and to adjust the refraction. When the total content of the RO components is too large, the devitrification resistance of the glass is likely to be deteriorated. The chemical durability of the glass is also likely to deteriorate. Therefore, the upper limit of the total content of the R 〇 component is preferably set to 35.0%, more preferably 25% by weight, and still more preferably 15. 〇%, based on the total mass of the glass of the oxide-converted composition. The best is 10.0%. In the optical glass of the present invention, the ratio of the content of the Ba0 component to the total content of the RO component is preferably 0 or more. Thereby, the content of the Ba〇 component which lowers the partial dispersion ratio and increases the refractive index is relatively large, so that the light having a relatively small partial dispersion and a high refractive index can be easily obtained. I63468.doc 201249769. Therefore, the lower limit of the molar ratio Ba 〇 / R 氧化物 of the oxide-converted composition is preferably 0.20, more preferably 0.30, still more preferably 0.40, most preferably 0.50. On the other hand, the upper limit of the molar ratio Ba〇/R〇 can be 〇〇.

The NaaO component is a component which increases the meltability of the glass, and at the same time lowers the component of the glass transition point (Tg), and is an arbitrary component in the optical glass of the present invention. In particular, by setting the content of the NazO component to 25.0% or less, it is easy to achieve a high refractive index, and at the same time, chemical durability is not easily deteriorated. Further, the devitrification resistance at the time of glass formation can be improved, and devitrification or coloration upon reheating can be reduced. Therefore, the upper limit of the content of the glass component of the oxide-converted composition is preferably set to 25 〇%, more preferably 20.0%, still more preferably 15 〇%, and most preferably 13 〇. %. Further, in the present invention, the NkO component may be contained from the viewpoint of further improving the resistance to devitrification of the glass. In this case, the lower limit of the content of the NaaO component is preferably set to more than 〇%, more preferably 0.3% Å, and still more preferably 0.5 Å/〇, based on the total mass of the glass of the oxide conversion composition. As the Na2〇 component, Na2C〇3, NaN03, NaF, Na2SiF6 or the like can be used as a raw material. The composition adjusts the meltability of the glass and lowers the component of the glass transition point (Tg), and is an optional component in the optical glass of the present invention. In particular, by setting the content of the K2 bismuth component to 25.0% or less, the devitrification resistance at the time of glass formation can be improved, and devitrification or coloring at the time of reheating can be reduced. Therefore, the upper limit of the content of the Κ2〇 component is preferably 25.0%, more preferably 2 〇·〇, with respect to the total mass of the glass of the oxide-converted composition. /. More preferably, it is 15.0%. Here, since the κ:2〇 component has a function of making the partial dispersion ratio less likely to be lowered, in particular, the viewpoint of obtaining a glass having a relatively low partial dispersion is 163468.doc •19·201249769 The upper limit of the content of the Κ2〇 component is also It is preferably set to 1 〇〇%, more preferably 5.0 °/. More preferably, it is 2.5°/. The optimum composition of 0.1 κ 2 可使 can be used as raw materials such as K2C03, ΚΝ〇3, KF, KHF2, K2SiF6 and the like.

The ChO component is a component which lowers the glass transition point (Tg) and is an optional component in the optical glass of the present invention. In particular, the content of the CkO component was set to 10.0. /. The following 'can reduce the devitrification of the glass caused by the excess of the Cs2 component. Therefore, the upper limit of the content of CS2 is preferably set to 10.0%, more preferably 5.0%, still more preferably 3.0%, based on the total mass of the glass of the oxide-converted composition. As the Cs2〇 component, Cs2c〇3, CsN03 or the like can be used as a raw material. In the optical glass of the present invention, the sum of the contents of the gRhO component (wherein Rn is selected from the group consisting of Li, Na, K and Cs) is 30.0% or less. In particular, by setting the molar ratio to 3% or less, the desired high refractive index can be easily obtained, and at the same time, the glass can be reduced. Therefore, the upper limit of the molar content of the Rn2〇 component is preferably set to 3 〇%, more preferably 28.0, based on the total mass of the glass of the oxide-converted composition. /. , and $ is better than 25.G%, and the best is 22 G%. The optical glass of the present invention may not contain any -Rn2〇 component, but by setting the sum to 〇"% or more", the glass transition property can be improved and the viscosity of the glass melt and the glass transition point during molding can be reduced. ... Thereby, the resistance to devitrification during reheating can be improved. Therefore, the lower limit of the mash content of the Rn20 forming knives is preferably set to 〇1%, more preferably 1, 〇%, and still more preferably 5.0%, based on the total mass of the glass of the oxide-converted composition. 10.〇%. The p2〇5 component is a component which enhances the stability of the glass and is an optional component in the optical 163468.doc -20- 201249769 glass of the present invention. In particular, when the content of the P2〇5 component is 30.0% or less, the devitrification tendency caused by the excessive content of the P2〇5 component is reduced. Therefore, the stability of the glass can be improved. Therefore, the glass is converted into an oxide composition. The upper limit of the total mass, the content of the Ρ2〇5 component is preferably set to 30.0%, more preferably 20.0%, and most preferably 10.0%. β ρ2〇5 component can be used Α1(Ρ03)3, Ca(P〇3) 2. Ba(P〇3)2, ΒΡ〇4, η3Ρ〇4, etc. are used as raw materials. ’,

The Ge 2 component is a component which increases the refractive index of the glass and reduces devitrification when the glass is stabilized and formed, and is an optional component in the optical glass of the present invention. In particular, by setting the content of the Ge 〇 2 component to 2 〇〇〇 / 〇 or less, the use amount of the expensive Ge 〇 2 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 set to 2%·〇%, more preferably 丨〇〇%, and still more preferably 5.0%, based on the total mass of the glass of the oxide-converted composition. It is 3.0%. As the Ge〇2 component, Ge〇2 or the like can be used as a raw material. The Y2〇3 component, the Gd2〇3 component, and the Yb2〇3 component are components which increase the refractive index of the glass, and are arbitrary components in the optical glass of the present invention. In particular, by setting the content of the 丫2〇3 component, the Gd2〇3 component, and the Yb2〇3 component to 15 〇% = respectively, the devitrification resistance of the glass can be improved, and the Abbe number of the glass can be made difficult to mention two. . Therefore, the upper limit of the content of each of the Y2〇3 component, the Gd2〇3 component, and the Yb2〇3 component is preferably set to 15·〇%', more preferably 10.0%, based on the total mass of the glass of the oxide conversion composition. The best is 5.0%. Y2〇3 can be used as Gd2〇3 component and Yb2〇3 component, GdF3, 丫2〇3, YI?3, Yb2〇3, etc. as raw materials.

The Ta2〇5 component is a component which increases the refractive index of the glass and lowers the partial dispersion 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 Ta2〇5 component to 15% or less, the amount of the Ta2〇5 component which is a rare mineral resource is reduced, and at the same time, the glass is easily melted at a lower temperature, thereby reducing the production of glass. cost. Further, by setting the content of the component of the dinosaur 5 as 15% or less, the devitrification resistance of the glass can be maintained. Therefore, the upper limit of the content of the TaA5 component is preferably set to 15% by weight, more preferably 10.0%, and most preferably 50%, based on the total mass of the glass of the oxide-converted composition. As the Ta2〇5 component, Ta2〇5 or the like can be used as a raw material.

The Biz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 lowers the composition of the glass transition point (Tg). In particular, by setting the content of the Bi2〇3 component to 15% by weight 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% or less, the coloring 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 BhO3 component is preferably set to 15% by weight, more preferably 10.0%, based on the total amount of the glass of the oxide-converted composition. The best is 5.0%. As the Bi2〇3 component, 2〇3 or the like can be used as the raw material. The W〇3 component is a component which is an optical glass of the present invention which is a component which increases the refractive index of the glass and lowers the Abbe number, improves the devitrification resistance of the glass, and improves the meltability of the glass. In particular, the content of the w〇3 component was set to 20.0. /. Hereinafter, the partial dispersion ratio of the glass crucible can be made difficult to rise. Further, by setting the content of the W〇3 component to be %, 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 20.0/〇, more preferably i〇.〇〇/〇, with respect to the total mass of the glass composed of the oxide conversion I63468.doc -22· 201249769. Good is 5 〇%. Further, since the component is an optional component, it may not be contained. However, by containing 〇1% or more of the w〇3 component, a glass having a smaller Abbe number can be obtained. Further, the devitrification resistance at the time of glass formation can be improved, and devitrification or coloration upon reheating can be reduced. Therefore, the lower limit of the content of the component with respect to the total mass of the glass of the oxide-converted composition is preferably set to 0.1%, more preferably 5%, and most preferably i 〇%. For the w〇3 component, W03 or the like can be used as a raw material.

The Te〇2 component is a component which increases the refractive index of the glass and lowers the partial dispersion ratio of the glass, and lowers the glass transition point (Tg), and is an optional component in the optical glass of the present invention. In particular, the transmittance of the glass with respect to visible light can be improved by setting the content of the Te02 component to 30.0% or less to reduce the color of the glass. Further, by reducing the use of the expensive Te〇2 component, it is possible to obtain a glass having a lower material cost. Therefore, the upper limit of the content of the Te〇2 component relative to the oxide-converted composition is preferably set. It is 3〇〇%, more preferably 20.0%, and most preferably 1%. 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 increases the refractive index of the glass, improves the resistance to devitrification, and lowers the partial dispersion ratio of the glass. In particular, by setting the content of the ZrO 2 component to 15.0% or less, the glass can be easily melted at a lower temperature, 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%, more preferably 12%, and most preferably 10.0%, relative to the total mass of the glass in terms of oxide conversion composition. Zr〇2 component, but by containing Zr〇2 163468.doc -23- 201249769 The composition is more than 〇%, the glass fold (4) can be increased, and the partial dispersion ratio of the glass can be easily further reduced. Further, by this, devitrification or coloration upon reheating can be reduced. Therefore, the lower limit of the content of the Zr〇2 component may be preferably set to more than 〇%, more preferably 1.0%, still more preferably 4.% by weight, and further more, relative to the total mass of the glass of the oxide-converted composition. The best is 45%, and the best is more than 5.5〇/〇. As the ZrO 2 component, Zr 〇 2, ZrF 4 or the like can be used as a raw material.

The Ah〇3 component is a component which improves the chemical durability of the glass and improves the resistance of the glass to the glass, and is an optional component in the optical glass of the present invention. In particular, by setting the content of the Ah 〇 3 component to 15.5% or less, the devitrification caused by the excessive content of the a 丨 2 〇 3 component can be reduced. Thereby, the devitrification or coloring at the time of reheating can be reduced. Therefore, the upper limit of the content of the AU〇3 component is preferably set to the total mass of the glass of the oxide-converted composition. 〇%, more preferably 10.0%, and most preferably 5.0%. As the raw material of a12〇3, Al2〇3, A1(〇H)3, A1F3 or the like can be used as a raw material.

The Sb2〇3 component promotes defoaming of the glass and clarifies the composition of the glass, and is an optional component in the optical glass of the present invention. By setting the amount of Sfc>2〇3 to 3 〗/〇 with respect to the total mass of the glass, it is possible to prevent excessive foaming when the glass is dazzled, and it is difficult to dissolve the Sb203 component. Equipment (especially precious metals such as Pt) is alloyed. Therefore, the upper limit of the content of the 8152〇3 component is preferably 1.0·. ‘More preferably 〇.8%, and even better 〇 6%. However, in the case of focusing on the influence of the optical glass on the environment, it is preferred that the #sb203 is not included. As the raw material, Sb2〇3, Sb2〇5, Na2H2Sb2〇7.5H2〇 or the like can be used as the Sb2〇3 component. Further, the component for clarifying the glass and defoaming is not limited to the above-mentioned %03 to 163468.doc •24 to 201249769, and a clarifying agent or a defoaming agent known in the field of glass production, or a combination thereof may be used. In the optical glass of the present invention, the ratio of the content of the B2〇3 component to the content of the Si〇2 component is preferably 丨.00. Since the si〇2 component is a component which is easy to deteriorate the meltability of the glass compared with the B2〇3 component, the melting at a high temperature is avoided by reducing the ratio, whereby the glass having less coloration can be easily obtained. By reducing the ratio, chemical durability or devitrification caused by reheating can also be improved. Therefore, the upper limit of the molar ratio (BaCVSiO2) of the oxide-converted composition is preferably set to 丨〇〇, more preferably 〇 8 〇, and most preferably 0.50. &lt;About the component which should not be contained&gt; Next, the component which should not be contained in the optical glass of the present invention and the component which is unsatisfactory are 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, transition metal components such as V, Cr, Mn, Co, Ni, Cu, Ag, and Mo have coloring and absorbing the glass even when they are contained in a small amount individually or in combination. The nature of the light of a particular wavelength of the visible field is therefore 'preferably substantially absent, especially in optical glass using wavelengths in the visible region. Furthermore, the arsenic compounds such as lead compounds such as Pb〇 and As2〇3, and the components of several, Cd, Tl, 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, environmental measures 163468.doc •25- 201249769 are required for the processing steps and until the post-product processing. Therefore, in the case of the influence of Yu Chongcuo 4 in terms of Yuan Jing, it is preferable that the quality is not included in the management except for the inevitable mixing. Thereby making light

The glass becomes essentially free of dirt and material that is used in the environment. Therefore, the optical glass can be manufactured, processed, and discarded without resorting to the lack of special environmental measures. It is preferably used as the glass of the optical glass of the present invention, and its composition is expressed by mol% of the total mass of the glass in terms of oxide composition, and therefore is not directly described as % by mass, and satisfies the requirements of the present invention. The composition represented by the mass % of each component present in the glass composition of each characteristic is approximately the following value in terms of oxide conversion composition.

Si〇2 component 5·0~30.0% by mass

The BaO component exceeds 〇 mass% to 35. 〇 mass 〇 / 0 La 2 〇 3 component exceeds 〇 mass. /. ～45·〇% by mass and Nb2〇5 components exceeding 0% by mass to 50.0% by mass and

Li2〇 composition 0~5.0 mass. /〇 and/or Ti02 component 0 to 15.0% by mass and/or B2O3 component 〇~30.0% by mass and/or MgO component 0 to 5.0% by mass and/or CaO component 0 to 1〇. /0 and / or SrO component 0 to 20.0% by mass and / or ZnO component 0 to 25.0 mass. /〇 and/or Na20 component 0~15.0% by mass and/or K20 component 0~25.0% by mass and/or 163468.doc • 26- 201249769

CszO composition 〇 ~ 25 · 〇 quality. /〇 and/or P2〇5 component 0~3 0.0% by mass and/or Ge02 component 〇~2〇.〇Quality 〇/〇 and/or Y2〇3 component 0~30·0 mass. /〇 and/or Gd203 component 〇~40.0% by mass and/or Yb2〇3 component 〇~40.0% by mass and/or Ta205 component 〇~5〇.〇% by mass and/or Bi2〇3 component 0~50.0% by mass and / or WO3 ingredients 〇 ~ 3 〇 〇 quality. /. And / or Te02 ingredients 〇 ~ 45.0 quality. /0 and / or Zr 〇 2 components 〇 ~ 20.0% by mass and / or Al2 〇 3 components 〇 ~ 20.0% by mass and / or Sb»2 〇 3 components 〇 ~ 3.0 mass 〇 / 〇 with oxides, the following The quality of the ingredients. The composition of /〇 indicates the conversion composition, which can also be the following range.

BaO composition exceeds 〇 mass ❶ / 〇 ~ 3 〇 〇 mass%

Nb205 component exceeds 〇 mass%~5〇 〇 quality Li2〇 component 0~4.0% by mass

Ti〇2 component 0 to 15.0% by mass 62〇3 component 〇~30. 〇% by mass. The composition of the following components by mass% may be the following range.

BaO composition exceeds 〇 mass%~35 〇 mass%

Nb2〇5 component exceeds 0% by mass to 50.0% by mass 163468.doc •27- 201249769

Li2〇 component 0 to 5.0% by mass Ti〇2 component 0 to 13.0% by mass B2O3 component 0 to 15.0% by mass [Production method] The optical glass of the present invention can be produced, for example, in the following manner. In other words, the raw materials are uniformly mixed in a range of the content of each of the knives, and the prepared mixture is poured into a platinum crucible, a stone crucible, or an alumina crucible for coarse melting. It is placed in a gold crucible, platinum crucible, platinum alloy crucible or silver. In the temperature range of ~Moot, it is condensed for 3 to 5 hours, and homogenization is carried out. After defoaming, it is set at 1000~ After the temperature, 'fine (four)' removes the vein pattern, and (4) the person's mold is slowly cooled, thereby producing an optical glass. &lt;Physical Properties&gt; 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 (6) of the optical glass of the present invention is preferably set to i.70, more preferably 1.759, and most preferably U0. Further, the upper limit of the refractive index (6) of the optical glass of the present invention is not particularly limited, and is usually about 2.20 or less, more specifically 21 Å or less, and further more preferably β is 2 〇〇 or less. Further, the upper limit of the Abbe number (6) of the optical glass of the present invention is preferably set to 4 Å, more preferably 38, still more preferably 35, and most preferably 3 3 . 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 20 or more, more specifically 23 or more, and furthermore. It is 25 or more. By this, the degree of freedom of the optical design is expanded, and even if the component is thinned, the amount of refraction of the larger light can be obtained. 163468.doc -28- 201249769 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 (-0.00162xvd+0.63822)^ (0g » F) in the range of vdS 31 The relationship of ^ (-0.00275xvd + 0.68 125), and satisfies the relationship of (·0.00162xvd+0.63822) S (eg, F)S (-0.00162xvd+0.64622) in the range of vd &gt; Thereby, an optical glass having a partial dispersion ratio (0g, F) close to a regular line can be obtained, so that chromatic aberration of the optical element formed of the optical glass can be reduced. Here, the lower limit of the partial dispersion ratio (0g, F) of the optical glass at the time of vdS31 is preferably

(-0.00162xvd+0.63822) ‘ More preferably (_〇.〇〇i62xvd+0.63922), the best is (-0.00162xvd+0.64022). On the other hand, the upper limit of the partial dispersion ratio (0g 'F) of the optical glass at Vd$31 is preferably (-0.00275 X vd + 0.68125) 'better (-〇.〇〇275xvd+(K68025), the best It is (-0.00275χν&lt;1+0·67925). Further, the lower limit of the partial dispersion ratio (0g, F) of the optical glass at Vd&gt;3l is preferably (-〇.〇〇i62xvd+0.63822), more preferably (-0.00162xvd+0.63922) 'Best is (_〇〇〇162xvd+〇64〇22). On the other hand, the upper limit of the partial dispersion ratio (0g, F) of the optical glass at Vd&gt;31 is preferably (- 0.00162xvd+0.64622), more preferably (_〇.〇〇i62xvd+ 0.64522), the best is (-〇.〇〇i62xvd+〇.64422). Furthermore, especially in areas with small Abbe number (vd) , the partial dispersion ratio of ordinary glass, F) is higher than the regular line value, and the partial dispersion ratio of ordinary glass (0g, ^ and Abbe number (vd) is represented by a curve. However, since the curve is approximated Difficult, so in the present invention, a straight line having a different slope as a boundary indicates that the partial dispersion ratio (eg, F) is lower than that of ordinary glass 163468.doc •29·201249769 Further, the optical glass of the present invention is preferably less colored. In particular, the optical glass of the present invention, when expressed by the transmittance of glass, exhibits a wavelength of 70% of light transmittance (λ? The thickness of 500 nm or less is more preferably 470 nm or less, more preferably 450 nm or less, and most preferably 43 Å or less. Further, the optical glass of the present invention is expressed by the transmittance of glass, and the thickness is 10 mm. The sample shows a wavelength at which the spectral transmittance is 80% (9: 8) is below 56 () nm, more preferably below 540 nm, and most preferably below 520 nm. Further, the optical glass of the present invention has a thickness of 10 mm. The sample shows a wavelength of 5% of the light transmittance (λ5) of 420 nm or less, preferably 400 nm or less, and most preferably 380 nm or less. Thereby, the absorption end of the glass is located near the ultraviolet region, and the glass in the visible region is visible. The transparency is improved. Therefore, the optical glass can be preferably used as a material of an optical element such as a lens. Further, the optical glass of the present invention preferably has good extrusion moldability. That is, the optical glass of the present invention is preferably reheated. After the test (2), the test piece has a wavelength of 587.56 nm. The transmittance of (d line) divided by the transmittance of the d line of the test piece before the reheating test is 095 or more. Further, it is preferable that the transmittance of the test piece before the reheating test (2) becomes 7〇. The wavelength of 0/〇 is λ7〇 and the λ? of the test piece after the reheating test. The difference is below 20 nm. Therefore, even if the reheating test of the assumed reheat extrusion processing is performed, the devitrification and coloring are less likely to occur, whereby the light transmittance of the glass is not easily lost, so that the glass can be easily represented by reheat extrusion processing. Heat 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. 163468.doc •30· 201249769 Here, the transmittance of the test piece after the reheating test (2) &lt;wavelength of wavelength 587 56 (10) (d line) is divided by the d line of the test piece before the reheating test (2) The lower limit of the value obtained by the transmittance is preferably set to 0.95', more preferably 〇96, and most preferably 〇97. X, the upper limit of the test piece before the reheat test (2) and the test piece after the reheat test (2) is preferably set to 20 • nm 'better 18 nm 'best Further, the reheating test (2) was carried out by reheating the test piece 15 mm x 15 mm x 30 mm, and heating from room temperature for 15 minutes to a temperature higher than the transfer temperature (Tg) of each sample. (The temperature of rc is kept at a temperature 80t higher than the glass transition temperature (Tg) of the optical glass for 3 minutes, and then naturally cooled to normal temperature, and the opposite sides of the test piece are ground to a thickness of 10 mm. Visual observation. [Preform and optical element] A glass molded body can be produced by a method of extrusion molding of an optical glass to be produced, for example, by re-extrusion molding or precision extrusion molding, that is, it can be made of optical glass. A preform for mold extrusion molding, which is subjected to reheat extrusion molding, and then subjected to a polishing process to produce a glass molded body or, for example, a precision compaction of a preform produced by polishing. Forming, Further, the glass molded body is not limited to these means. The glass molded body thus produced is useful for various optical elements, among which 'especially for optical elements such as lenses or iridium. The use of the optical system provided with the optical element reduces the blurring of the color caused by the chromatic aberration. Therefore, when the optical element is used in a camera, 163468.doc 31 201249769 When the photographic object is correctly displayed, when the optical element is used in the photographic device, the desired image can be projected with great brilliance. [Embodiment] Embodiments of the present invention (No. 1 to No) .33) and comparative examples (n〇.a to No.d), and refractive index (nd), Abbe number (Vd), partial dispersion ratio (0g, F), spectral transmittance show 5%, 70 The fluctuations of the transmittances of % and 80% (λ5, human 7〇, λβο), and before and after the reheating test (2) are shown in Table 6. Further, the following examples are merely illustrative, the present invention It is not limited to the embodiments. Embodiments of the invention (1^〇. 1~&gt;1〇.33) and the comparative examples (]^0.8~1^0.1)) are all selected from the respective oxides, hydroxides, carbonates, sulphates, II compounds, and hydroxides. A high-purity raw material used in a usual optical glass such as a substance or an acid-filled compound is used as a raw material of each component, and is weighed so as to become a ratio of the composition of each of the examples and the comparative examples shown in Tables to Table 6, and After uniformly mixing, it is put into a platinum crucible, and melted in an electric furnace at a temperature of 1100 to 1400 t for 3 to 5 hours according to the melting difficulty of the glass composition, and stirred and homogenized, and after defoaming, etc., it is set at 1000. After homogenization by stirring at 1400 ° C, it was cast into a mold and slowly cooled to prepare a glass. Here, the refractive index (in), Abbe's number (vd), and partial dispersion ratio (0g, F) of the glass of the examples (No. 1 to No. 33) and the comparative examples (No. A to No. D) It is measured based on the specifications of the 光学本光光子工业会jOGIS01-2〇03. Further, for the values of the obtained Abbe number (vd) and the partial dispersion ratio (eg, F), the relationship (eg, F) = -axvd + b is obtained, and the slope a is 0·00162 and 〇〇〇275 hours 163468.doc -32- 201249769 Intercept b. Further, the glass used in the measurement was subjected to a slow cooling rate of -25 ° C /hr, and was treated by a slow cooling furnace. Further, the transmittances of the glass of the examples (No. 1 to No. 33) and the comparative examples (No. A to No. D) were measured in accordance with the specifications of the 光学 光学 硝 。 。 。 。 。 。 。 。 。. 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, the opposite surface of the thickness is 丨〇±〇"mm, and the article is measured in accordance with JIS Z8722. The light transmittance of 〇〇8〇〇(10) is determined as the wavelength at which the transmittance is 5%), λ7〇 (the wavelength at which the transmittance is 7〇%), and λ8〇 (the wavelength at which the transmittance is 80%). Further, the changes in transmittance before and after the reheating test (2) of the glass of Examples (No. 1 to No. 33) and Comparative Examples (No. A to No. D) were measured as follows. The transmittance obtained by dividing the transmittance of the test piece after the reheating test (2) with the wavelength of 587, 56 nm by the transmittance of the d line of the test piece before the reheating test is for the reheating test (2) The glass before and after is carried out according to the specifications of the Japan Optical Glass Industry Association jOGIS02_2003. Specifically, for the opposite surface parallel polished product having a thickness of 10 ± 0.1 mm, the spectral transmittance of the ridge line is measured in accordance with JIS Z8722, and the (d-line transmittance after reheating test (2)) is obtained (reheating test (two) The d-line transmittance of the front) was evaluated for the change in the maximum transmittance before and after the reheating test (2). On the other hand, the transmittance of the test piece before the reheating test (II) becomes 70 〇 / 波长, that is, the difference between the 7 〇 and the test piece after the reheating test is the glass before and after the reheating test (2) Using the above test method to determine ?w〇 (wavelength at 70°/. transmittance), and evaluate the test before reheat test (2) 163468.doc •33·201249769 λ7〇 and reheat test (2) The difference between the λ7〇 of the subsequent test piece. Here, the reheating test (2) is carried out by placing a test piece of i 5 mm×l5 mm×30 mm on a concave refractory, placing it in an electric furnace for reheating, and heating from a normal temperature for 15 minutes. The transfer temperature (Tg) of each sample is 8 (the temperature of TC (the temperature in the refractory), and after holding at this temperature for 30 minutes, it is cooled to normal temperature and taken out to the outside of the furnace. After grinding to a thickness of 1 〇 mm on both sides, the ground glass sample was visually observed. 163468.doc • 34_ 201249769 [Table 1] Example 1 2 3 4 5 6 7 8 Si02 36.50 36.50 36.50 36.50 36.50 36.50 32.80 36.50 BaO 6.40 6.40 6.40 6.40 6.40 6.40 6.40 6.40 L&2〇3 6,40 6.40 6.40 6.40 6.40 6.40 6.40 6.40 Nb2〇5 9.60 9.60 11.52 7.68 3.84 9.60 9.60 15.36 Li20 9.00 9.00 9.00 9.00 9.00 9.00 9.00 9.00 Ti02 9.60 9.60 7.68 11.52 15.36 9.60 9.60 3.84 Na20 11.00 11.00 11.00 11.00 11.00 11.00 11.00 11.00 K20 MgO CaO SrO ZnO P2〇5 B]03 4.50 4.50 4.5 0 4.50 4.50 4.50 8.20 4.50 Y203 Gd2〇3 Yb203 T&2〇5 Bi203 W〇3 Zr02 7.00 7.00 7.00 7.00 7.00 7.00 7.00 7.00 ai,o3 Sb203 0.01 0.01 0.01 0.01 0.01 0.01 0.01 Total 100.0 100.0 100.0 100.0 100.0 100.0 100.0 100.0 La+Ba/Nb+Ti 0.667 0.667 0.667 0.667 0.667 0.667 0,667 0.667 Ti/Nb 1.000 1.000 0.667 1.500 4.000 1.000 1.000 0.250 Nb/(Si+B) 0.234 0.234 0.281 0.187 0.094 0.234 0.234 0.375 Li+Na+K 20.00 20.00 20.00 20.00 20.00 20.00 20.00 20.00 Mg+Ca+Sr+Ba+Zn 6.40 6.40 6.40 6.40 6.40 6.40 6.40 6.40 Ba/(Mg+Ca+Sr+Ba+Zn) 1.000 1.000 1.000 1.000 1.000 1.000 1.000 1.000 B/Si 0.123 0.123 0.123 0.123 0.123 0.123 0.250 0.123 nd 1.83890 1.83898 1.84757 1.82983 1.81075 1.83892 1.83835 1.86402 Vd 30.1 30.1 29,7 30.5 31.4 30.1 30.0 29.0 6g * F 0.5939 0.5944 0.5958 0,5942 0.5930 0.5956 0.5953 0.5985 Load distance b (a=-0.〇〇162) 0.64267 0.64324 0.64391 0.64361 0.64390 0.64438 0.64394 0.64550 Intercept 1^=-0.00275) 0.67668 0.6772 5 0.67747 0.67807 0.67939 0.67840 0.67784 0.67827 λβοΓητη] 472 460 460 456 454 481 475 475 λ7〇[ητη1 411 405 404 404 405 414 412 407 λ5[ηηι1 353 351 351 352 353 353 353 349 Test (II) Post-transmission rate / test ( 2) &amp; pass-through test (2) after λ70-test (2) before 163468.doc -35- 201249769 [Table 2] Real "Package example 9 10 11 12 13 14 15 16 Si02 32.80 36.50 36.50 36.50 36.50 34.50 36.50 36.50 BaO 6.40 6.40 6.40 6.40 6.40 6.40 4.40 8.40 La2〇3 6.40 6.40 640 6.40 6.40 6.40 6.40 4.40 Nb2〇s 15.36 9.60 11.52 9.60 9.60 9.60 9.60 11.52 Li20 9.00 9.00 9.00 7.00 9.00 9.00 9.00 9.00 Ti02 3.84 9.60 7.68 9.60 9.60 9.60 9.60 7.68 Na20 11.00 11.00 11.00 11.00 9.00 11.00 11.00 11.00 K20 MgO CaO SrO ZnO P2〇5 B2O3 8.20 4.50 4.50 6.50 6.50 6.50 6.50 4.50 y2〇3 Gd203 Yb2〇3 T&amp;2〇5 Bi203 W03 Zr〇2 7.00 7.00 7.00 7.00 7.00 7.00 7.00 7.00 Al2〇 3 Sb2〇3 0. 01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 Total 100.0 100.0 100.0 100.0 100.0 100.0 100.0 100.0 La+Ba/Nb+Ti 0.667 0.667 0.667 0.667 0.667 0.667 0.563 0.667 Ti/Nb 0.250 1.000 0.667 1.000 1.000 1.000 1.000 0.667 Nb/(Si+B 0.375 0.234 0.281 0.223 0.223 0.234 0.223 0.281 Li+Na+K 20.00 20.00 20.00 18.00 18.00 20.00 20.00 20.00 Mg+Ca+Sr+Ba+Zn 6.40 6.40 6.40 6.40 6.40 6.40 4.40 8.40 Ba/(Mg+Ca+SH-Ba+ Zn) 1.000 1.000 1.000 1.000 1.000 1.000 1.000 1.000 B/Si 0.250 0.123 0.123 0.178 0.178 0.188 0.178 0.123 nd 1.86360 1.83875 1.84764 1.83524 1.83997 1.83789 1.83267 1.84020 Vd 28.9 30.1 29.7 29.9 30.0 30.0 30.0 29.3 0g,F 0.5981 0.5944 0.5952 0.5924 0.5939 0.5927 0.5933 0.5960 Intercept b(a=-0.00162) 0.64501 0.64324 0.64335 0.64091 0.64253 0.64137 0.64197 0.64349 Load distance b(a=-0.00275) 0.67767 0.67725 0.67691 0.67470 0.67643 0.67527 0,67587 0.67659 λ8〇Γητη] 489 462 468 455 459 454 452 470 λ7〇 [ητη] 413 405 405 402 404 402 402 411 λ5[ηηι] 350 352 351 353 353 351 352 353 After the test (2) transmittance / test (2) before the transmittance test (2) after λ7 〇 _ test (b) before λ70 -36- 163468.doc 201249769 [Table 3] Example 17 18 19 20 21 22 23 24 Si02 36.50 38.50 40.50 41.50 43.00 46.00 46.00 43.55 BaO 6.40 6.40 6.40 6.40 6.40 6.40 6.40 6.06 L&amp;2〇3 6,40 6.40 6.40 6.40 6.40 8.40 6.40 7.96 Nb205 9.60 9.60 9.60 9.60 9.60 7.60 7.60 7.19 Li20 9.00 9.00 9.00 9.00 9.00 9.00 9.00 18.76 Ti02 9.60 9.60 9.60 9.60 9.60 9.60 9.60 9.09 Na20 9.00 9.00 9.00 9.00 9.00 6.00 6.00 0.75 K20 MgO CaO 2.00 SrO ZnO P2〇5 b2o3 6.50 4.50 2.50 1.50 Y2〇3 Gd2〇3 Yb2〇3 T&amp;2〇5 Bi2〇3 W〇3 Zr02 7.00 7.00 7.00 7.00 7.00 7.00 7.00 6.63 Al2〇3 Sb2〇3 0.01 0.01 0.01 0.01 0.01 0.01 0.01 Total 100.0 100.0 100.0 100,0 100.0 100.0 100.0 100.0 La+Ba/Nb+Ti 0.667 0.667 0.667 0.667 0.667 0.860 0.744 0.861 Ti/Nb 1.000 1.000 1.000 1.000 1.000 1.263 1.263 1. 264 Nb/(Si+B) 0.223 0.223 0.223 0.223 0.223 0.165 0.165 0.165 Li+Na+K 18.00 18.00 18.00 18.00 18.00 15.00 15.00 19.51 . Mg+Ca 十 SrfBa+Zn 6.40 6.40 6.40 6.40 6.40 6.40 8.40 6.06 EJa/(Mg+ Ca+Sr+Ba+Zn) 1.000 1.000 1.000 1.000 1.000 1.000 0.762 1.000 B/Si 0.178 0.117 0.062 0.036 0.000 0.000 0.000 0.000 nd 1.84019 1.84049 1.84064 1.84059 1.84069 1.83232 1.82436 1.83885 vd 30.0 30.0 30.0 30.1 30.1 31.8 31.5 32.4 0g 1 F 0.5960 0.5957 0.5927 0,5947 0.5946 0.5902 0.5904 0.5893 Load distance b(a=-0.00162) 0.64460 0.64439 0.64139 0.64354 0.64340 0.64180 0.64147 0.64184 Load distance b(a=-0.00275) 0.67850 0.67829 0.67529 0.67755 0.67741 0.67773 0.67706 0.67845 λ8〇[ηιη] 465 464 472 462 466 422 429 446 λ7〇[ηπι] 408 406 407 407 406 387 390 394 λ5[ηιτι] 354 353 353 354 353 351 352 349 After the test (2) transmittance / test (2) before the 'test (2) λ70- Test (2) before λ70 • 37 · 163468.doc 201249769 [Table 4] Example 25 26 Si02 43.21 39.75 BaO 6.01 6.06 L&amp;2〇3 7.90 5.9 6 Nb2〇5 7.14 9.19 Li20 20.14 18.76 Ti02 9.02 5.89 Na20 0.75 K2〇MgO CaO 2.00 SrO ZnO P2〇5 B2〇3 3.00 Y2〇3 Gd2〇3 Yb2〇3 Taj〇5 Bi2〇3 W〇3 2.00 Zr02 6.58 6.63 Al2〇3 Sb2〇3 0.01 0.01 Total 100.0 100.0 La+Ba/Nb+Ti 0.861 0.797 Ti/Nb 1.264 0.641 Nb/(Si+B) 0.165 0.215 Li+Na+K 20.14 19.51 Mg+Ca+S r+B a +Zn 6.01 8.06 Ba/(Mg+Ca+Sr+Ba+Zn) 1.000 0.752 B/Si 0.000 0.075 nd 1.83921 1.84081 Vd 32.5 31.5 0g · F 0.5887 0.5907 Intercept b (a=-0.00162) 0.64143 0.64180 Intercept b ( a=-0.00275) 0.67816 0.67740 λ8〇[ητη] 444 461 λ7〇[ηηι] 395 403 λ5[ηηι] 349 350 Test (2) Transmittance / Test (2) Front transmittance test (2) After λ7 £Γ Test (b) before λ70 · 38 · 163468.doc 201249769 [Table 5] Example 27 28 29 30 31 32 33 Si02 40.552 40.552 40.552 39.752 40.552 40.552 37.889 BaO 6.060 6.060 8.060 8.060 8.060 8.060 8.310 La2〇3 5.958 5.376 5,958 5.958 5.376 5.376 5.842 Nb2〇5 9.192 9.192 9,192 9.192 9.192 9,192 9.476 Li 20 18.761 18.761 18.761 18.761 18.761 14.761 17.279 Ti02 6.126 5.672 6.126 5.890 5.672 5.672 5.341 Na20 0.745 0.745 0,745 0.745 0.745 4.745 2.830 K20 MgO CaO 2.000 2.000 SrO ZnO P2〇5 B2O3 3.000 3.000 3.000 3.000 3.000 3.000 3.093 y2〇3 Gd2〇3 Yb203 Τ ^2〇5 Bi203 WO3 2.000 2.000 2.000 2.000 2.000 2.000 3.093 Zr02 5.595 6.631 5.595 6.631 6.631 6.631 6.836 AI2O3 Sb203 0.010 0.010 0.010 0.010 0.010 0.010 0.010 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 La+Ba/Nb+Ti 0.785 0.769 0.915 0.929 0.904 0.904 0.955 Ti/Nb 0.666 0.617 0.666 0.641 0.617 0.617 0.564 Nb/(Si+B) 0.211 0.211 0.211 0.215 0.211 0.211 0.231 Li+Na+K 19.506 19.506 19.506 19.506 19.506 19.506 19.506 Mg+Ca+Sr+Ba+Zn 8.060 8.060 8.060 8.060 8.060 8.060 8.060 Ba/(Mg+Ca+SrfBa+Zn) 0.752 0.752 1.000 1.000 1.000 1.000 1.000 B/Si 0.074 0.074 0.074 0.075 0.074 0,074 0.082 n&lt;j 1.83663 1.83465 1.83693 1.84087 1.83 417 1.82625 1.84363 vd 31.6 31.6 31.6 31.6 31.7 31-6 31.3 0g ' F 0.5913 0.5910 0.5910 0.5903 0.5907 0.5906 0.5911 Wearing distance b (a=-0.00162) 0.64251 0.64219 0.64227 0.64150 0.64209 0.64186 0.64188 Wearing distance b (a=-0.00275) 0.67822 0.67790 0.67798 0.67721 0.67791 0.67757 0.67725 λ8〇[ηπι] 458 454 458 460 462 453 457 λ7〇[ηιτι] 402 398 401 402 401 399 402 Xs[rm] 350 350 350 350 350 349 351 Test (2) Transmittance / Test ( 2) Pre-transmission rate 0.995 1.000 0.993 0.996 1.000 Test (2) After λ7 (Γ test (2) before λ70 2.0 1.5 1.5 -9,0 0Ό 163468.doc -39- 201249769 [Table 6] Comparative example ABCD Si02 28.47 14.43 5.33 9.23 BaO 1.04 1.55 La2〇3 1.55 3.85 3.69 2.31 Nb205 5.00 3.45 Li20 3.80 Ti02 11.43 11.01 19.05 19.83 Na20 1.63 K20 1.61 MgO 10.03 CaO 30.20 24.92 30.00 28.25 SrO 3.06 ZnO 8.16 5.91 P2〇5 B2O3 4.89 18.14 31.07 28.44 Y2O3 1.27 0.88 Gd: 〇3 Yb203 Ta205 Bi2〇3 W03 0.58 Zr02 4.58 5.26 3.90 2.57 ai2〇3 5.70 3.88 Sb2〇3 0.01 0.01 0.01 0.01 Total 100.0 100.0 100.0 100.0 La+Ba/Nb+Ti 0.095 0.266 0.248 0.195 Ti/Nb 2.287 3.189 - - Nb/(Si+B) 0.150 0.106 0.000 0.000 Li+Na+K 0.00 7.04 0.00 0.00 Mg+Ca+Sr+Ba+Zn 38.37 34.95 36.95 32.85 Ba/(Mg+Ca+SH-Ba+Zn) 0.000 0.000 0.028 0.047 B/Si 0.172 1.257 5.825 3.082 n&lt;i 1.81714 1.80608 1.81728 1.78840 Vd 32.1 34.2 32.6 33.2 0g 1 F 0.5944 0.5877 0.59450 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 λ80[ηηι] 461 454 478 474 λ7〇[ηηι] 408 402 422 418 λ5 [ηηι] 359 349 363 363 Test (II) Transmittance/Test (II) Front transmittance 0.000 0.111 0.998 1.000 Test (II) After λ7〇-Test (II) Before λ70 - - 1.0 2.0 I63468.doc • 40- 201249769 As shown in Tables 1 to 6, the partial dispersion ratio of the optical glass vds 31 of the embodiment of the present invention is hereinafter referred to as 〇〇〇 275xvd + 〇 68125 below. In more detail, it is (-〇. 〇〇 275xvd + 0.67850) below. Further, the partial dispersion ratio (0g, F) of vd &gt; 31 is (_〇 〇〇 162xvd + 〇 64622) or lower, and more specifically, (-〇.〇〇162xvd+0.64390) or less. On the other hand, the partial dispersion ratio (0g, F) of the optical glass of the embodiment of the present invention is (-0.00162xvd + 0.63822) or more, and more specifically, (_0 00162x vd + 0.64091) 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. Therefore, it is known that the partial dispersion ratios (eg, F) are within the desired range. On the other hand, the glass of the comparative example (N〇.A, No. C, No. D) of the present invention is vd&gt;31' partial dispersion ratio (0g, F) exceeds (_〇 〇〇 162xvd + 〇 64622). Therefore, it is understood that the optical glass of the embodiment of the present invention has a partial dispersion ratio, F) is smaller than that of the glass of the comparative example (N〇.A, No.C, No.D), and the embodiment of the present invention The refractive index (nd) of the optical glass is 17 Å or more, and more specifically, 1.81 or more. At the same time, the refractive index (nd) is 2, 20 or less, and more specifically, 187 or less. Within the expected range. Further, the optical glass of the embodiment of the present invention has an Abbe number (Vd) of 2 Å or more, more specifically 28 or more, and at the same time, the Abbe number (,) is 4 Å or less, and more specifically The statement is 33 or less and is within the expected range. On the other hand, the glass of the comparative example (N〇B) of the present invention exceeds 34. Therefore, it is found that the optical glass of the embodiment of the present invention has a smaller Abbe number (vd) than the glass of the comparative example (No. B). 163468.doc 41 - 201249769 Further, the λ7 光学 (wavelength at a transmittance of 70%) of the optical glass of the embodiment of the present invention is 500 nm or less 'more specifically 414 nm or less, and more specifically 407. Below nm. Further, the wavelength of the λ 〆 transmittance of the optical glass of the embodiment of the present invention is 420 nm or less, more specifically 359 nm or less, and more specifically 355 nm or less. Further, the present invention The λ8 光学 (wavelength at a transmittance of 80%) of the optical glass of the examples is 56 〇 nm or less, more specifically 489 nm or less, and more specifically 463 nm or less. Therefore, it is known that the optical glass of the embodiment of the present invention has a high transmittance with respect to visible light and is not easily colored. Therefore, it is known that the refractive index (η and the Abbe number (vd) of the optical glass of the embodiment of the present invention are within a desired range and the transmittance with respect to visible light is high' and the chromatic aberration is small. The transmittance of the d-line of the test piece after the reheating test (2) of the optical glass of the embodiment of the present invention is divided by the transmittance of the test line of the test piece before the reheating test, and the values obtained by the test are all above Q 95. More specifically, it is above ,^, and is within the desired range... The reheating test of the optical glass of the embodiment of the present invention (II) before and after the test piece t transmittance is less than 2 〇 nm. And r is 15 (10) or less, which is within the desired range. On the other hand, the d-line of the test piece after the reheating test (2) of the glass of the comparative example (No. A, No. B) of the present invention The transmittance is divided by the transmittance of the d-line of the test piece before the reheating test, and the value obtained is less than ,95. After the reheating test (2), the transmittance is not farther than 70 for all wavelengths of light. /〇. Therefore, I also know that the optical glass and ratio of the application of the moon The glass phase 屮 a 邗 ratio of the case (Νο.Α, Νο·Β) is not easy to produce the coloring caused by reheating 163468.doc -42- 201249769 or devitrification. Above, for the purpose of illustration τΛ μ The present invention is intended to be understood as being merely illustrative, and various practitioners may apply various changes without departing from the scope of the invention. [FIG. 1 is a simplified description] The partial dispersion ratio (eg, f) is the vertical axis and the Abbe number (Vd) is the normal line indicated by the orthogonal coordinates of the horizontal axis. Fig. 2 is a view showing a portion of the glass relating to the embodiment of the present application. A plot of the relationship between the dispersion ratio (Gg 'F) and the Abbe number (vd). 163468.doc •43·

Claims (1)

201249769 VII. Patent application scope: 1. An optical glass containing SiO2 component of 10.0% or more and 60.0% or less and BaO component of more than 0%, based on the total mass of the glass in terms of oxide conversion composition. 25.0% or less, La2〇3 component is more than 0〇/〇 and 15.0% or less, and Nb205 component is more than 0% and 20·0°/〇 or less, in partial dispersion ratio, F) and Abbe number (vd) In the range of vdS 31, the relationship of (-0.00162xvd+0.63822)^(0g &gt; F)^ (-0.00275xvd+0.68125) is satisfied, and is satisfied in the range of vd &gt; 31 (·〇.〇〇i62xvd+ 0.63822) S (eg, F) g (-0.00162xvd + 0.64622) relationship. 2. The optical glass of claim 1, wherein the total mass of the glass relative to the oxide-converted composition is more than 0% and 20.0% or less, and the Nb2〇5 component is more than 0% by mol%. % and less than 19.5%. 3. The optical glass according to claim 1, wherein the content of the LhO component is not less than 3 % by mol based on the total mass of the glass of the oxide conversion composition. 4. The total amount of the glass of the claim 1 is in the range of more than 〇% and 30.0% or less in terms of mol%. 5. The optical glass of the requester, wherein the total mass of the glass which is planted in terms of oxide is 20.0% of the Ti〇2 component in terms of mol%.禾禾达 6. As requested by the optical glass, which is based on the total mass of the oxide, in terms of mole %, the content of the ton component is (iv) to 163468.doc 201249769 7. Optical glass according to claim 1 The molar ratio (Ba0+La203)/(Nb205+Ti02) of the oxide conversion composition in ## is 〇.05 or more. 8. The optical glass of claim 1, wherein the molar ratio of the molar ratio Ti02/Nb2〇5 is 5.0 or less. 9. The optical glass of claim 1, wherein the content of the b2〇3 component is 4 〇 or less based on the total mass of the glass in terms of oxide conversion. 10. The optical glass of claim 1, wherein the content of the B2〇3 component is 2% or less based on the total mass of the glass in terms of oxide conversion. 11. The optical glass of claim ,, wherein the molar ratio of the molar ratio Nb205/(Si〇2+B203) is 0.070 or more. 12. The optical glass of claim 3, wherein the mass of the glass relative to the oxide-converted composition is 0 to 20.0% and/or the CaO composition 〇 20.0% and/or in terms of moir/〇 The SrO component is 220.0% and/or the ZnO component 〇30.0%. 13. As requested! The optical glass, the total mass of the glass in the bismuth relative to the composition of the oxide, and the RO component (wherein the ruler is selected from the group consisting of Mg, U, Sr, Ba, and Zn) And the sum is 35〇% or less. 14. The optical glass of claim 1 wherein the oxide is converted to a molar ratio of Ba 〇 / R 〇 (wherein R is selected from the group consisting of Mg, Ca, 〜 ', and consisting of 163468.doc 201249769 The above species is 0.20 or more. 15. The optical glass of the request, wherein the mass of the glass relative to the composition of the oxide is in terms of mole %, Na2〇 composition 〇~25.0% and/or, K2〇 composition 0~25.0% and/or Cs2〇 composition 〇~10.0%. 16. For the optical glass of the requester, the Rn20 component (wherein (10) is selected from the group consisting of u, Na, K, and Cs) The ear sum is below 3〇〇%. 17. The mass of the glass of the optical glass of the composition of the present invention, in terms of mol%, in terms of mol%, p2〇5 component 〇~30.0% and/or Ge〇2 component 0~20.0°/. And/or γ2〇3 component 0~15.0% and/or Gd2〇3 component 0~15.0% and/or Yb2〇3 component 0~15.0% and/or Ta2〇5 component 0~15.0% and/or Bi2〇3 Component 0~15.0% and/or * W〇3 component 〇~20 0% and/or. Te〇2 component 0~30.0% and/or Zr〇2 component 0~15.0% and/or A12〇3 component 0~ 15.0% and/or Sb2〇3 ingredients 0~1.0°/〇. 18. The Mohr ratio of 163468.doc 201249769 (B2〇3/Si02) of the optical glass of the requester is 1.00 or less. 19. As requested! The optical glass has a refractive index (nd) of 17 Å or more and 195 or less, and has an Abbe number (vd) of 20 or more and 40 or less. 20. The optical glass of claim ,, wherein the spectral transmittance shows that the wavelength of 7〇% (λ7〇) is 500 nm or less. 21. The optical glass of claim ,, wherein the transmittance of the light at the wavelength of 587.56 nm (d line) of the test piece after the reheating test (2) is divided by the test piece of the reheated s test before the test The value obtained by the transmittance of the line is 095 or more. [Reheating test (2): Reheating the test piece 15 mm x 15 mm x 30 mm 'The temperature is raised from room temperature for 150 minutes to a temperature higher than the transfer temperature (Tg) of each sample. The temperature of 80 ° C was kept at a temperature 80 ° higher than the glass transition temperature (Tg) of the optical glass for 30 minutes, and then naturally cooled to normal temperature, and the opposite sides of the test piece were ground to a thickness of 10 After mm, visual observation]. 22. The optical glass of claim 1, wherein the transmittance of the test piece before the reheat test (2) is 70%, that is, the difference between λ·7〇 and the λ70 of the test piece after the reheat test is 20 nm. Hereinafter, [reheating test (1). The test piece 15 mnixl5 mm&gt;&lt;30 mm was reheated, and the temperature was raised from room temperature for 15 minutes to a temperature higher than the transfer temperature (Tg) of each sample by 80 °C. 'The temperature is maintained at a temperature 80 ° C higher than the glass transition temperature (Tg) of the optical glass for 30 minutes, and then naturally cooled to room temperature, and the opposite sides of the test piece are ground to a thickness of 1 〇 mm, and then visually observed. Observed]. 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。. An optical component formed by grinding and/or grinding an optical glass according to any one of claims 1 to 3. An optical element formed by precisely extruding an optical glass according to any one of claims 1 to 22. 163468.doc