TW201231427A - Optical glass, preform, and optical element - Google Patents

Abstract

The purpose of the present invention is to provide an optical glass and a lens preform using the same, which has the refractivity (nd) and the Abbe number (νd) within a required range and is preferably applicable to correcting the chromatic aberration. An optical glass comprises B2O3 ingredient, which has the refractivity (nd) above 1.70 and the Abbe number (νd) above 39, and has a partial dispersion ratio (θg, F) which satisfies the relationship of Abbe number (νd): (θg, F) ≥ (-0.00170 × νd+0.63750) or (θg, F) ≥ (-2.0×10 -3 × νd+0.6498).

Description

201231427 VI. Description of the Invention: TECHNICAL FIELD The present invention relates to an optical glass, a preform, and an optical element. [Prior Art] Optical systems such as digital cameras or video cameras have a size to the left, but the bar is called the blur of aberrations. This aberration is classified into monochromatic aberration and chromatic aberration, and in particular, chromatic aberration strongly depends on the material properties of the lens used in the optical system. By #, chromatic aberration is corrected by combining a low-dispersion convex lens with a highly-dispersed concave lens, but this combination can only correct the aberration between the red region and the green region, and the aberration of the blue region remains. The aberration of the i color region which is not completely removed is referred to as a secondary spectrum. In order to correct the secondary spectrum, an optical design supplementing the g-line of the blue region (435.835 nm) must be performed. At this time, as an indicator of the optical characteristics that are attracting attention in the optical design, the partial dispersion ratio (eg'F) is used to combine the above-mentioned low-dispersion lens with the optical lens of the highly dispersed lens in the system, at a low level. The lens on the dispersion side uses a partial fractional ratio, F) a larger optical aperture, ν, ν ^ , and a lens on the high dispersion side using a fractional dispersion ratio (eg, F) of a smaller secondary light. The first sub-material, by which the eigen is well corrected, F=(ng-nF)/(nF-nc) ..... (1) (ng thinks that the glass is the source of mercury and the rate of radiation, nF means the glass family *, · / length is 435_835 surface spectrum line two of the refraction # ^ ^ source is hydrogen and the wavelength is 486.13 nm of the refractive index, nc means the refractive index of the broken spectrum line). The source is 虱 and the wavelength is 656.27 m 157771.doc 201231427 In optical glass, there is a roughly linear relationship between the partial dispersion ratio (eg, F) and the Abbe number (Vd) indicating the partial dispersion of the short wavelength band. The straight line indicating the relationship is a partial dispersion ratio (0 g, F) on the vertical axis and an Abbe number (vd) on the orthogonal axis on the horizontal axis. 'The NSL7 and pBM22 partial dispersion ratio and Abbe number will be drawn. The line connecting the two points is called a normal line (see Fig. 1). The regular glass system that becomes the basis of the regular line varies according to each optical glass manufacturer, but each company also defines it by the slope and intercept. (NSL7 and PBM2 are optical glass manufactured by OHARA Co., Ltd., the Abbe number (Vd) of PBM2 is 3 6.3, the partial dispersion ratio (0g, F) is 0.5828, and the Abbe number (Vd) of NSL7 is 60.5 'partially dispersed. The ratio (0g, F) is 0.5436). Here, as the glass having a higher refractive index (nd) of 1 to 73 or more and a higher Abbe number (lower dispersion) of 45 or more, for example, an optical glass as disclosed in Patent Documents 1 to 3 is known. Further, as a glass having a higher refractive index (nd) of 1.70 or more and a higher Abbe number (lower dispersion) of 39 or more and less than 52, for example, it is known that a large amount of La2〇3 is contained as shown in Patent Documents 4 to 6. An optical glass of a rare earth element component such as a component. Further, as the glass having a higher refractive index (nd) of 1.60 or more and 1 to 70 or less and a higher Abbe number (vd) of 5 or more, for example, an optical glass as disclosed in Patent Documents 7 to 10 is known. In addition, as a glass having a higher refractive index (nd) of 1.57 or more and a higher Abbe number (vd) of 5 Å or more, for example, it is known that a rare earth element component such as a large amount of La203 component is contained as shown in Patent Documents 11 to 19. Optical glass. [Patent Document 1] Japanese Patent Laid-Open Publication No. Hei. No. Hei. No. Hei. No. Hei. [Patent Document 4] Japanese Patent Laid-Open Publication No. Hei. No. Hei. No. Hei. No. 2006-016295 [Patent Document 6] International Publication No. 2004/054937 Japanese Laid-Open Patent Publication No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. Japanese Patent Laid-Open Publication No. Hei. No. Hei. No. 2007-261877 [Patent Document 12] Japanese Patent Laid-Open Publication No. 2009-084-59 (Patent Document 13) Japanese Laid-Open Patent Publication No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. Japanese Patent Publication No. 2005-170782 [Patent Document 17] Document 18] said present No. 2006-016295 Patent Laid-Open Publication.

[Patent Document 19] International Publication No. 2004/054937 [Explanation] [Problems to be Solved by the Invention] However, the optical glass systems of Patent Documents 1 to 19 have a small dispersion ratio, so

S 157771.doc 201231427 is not suitable for use as a lens for correcting the above secondary spectrum. That is, the manufacturer requires an optical glass having a low dispersion (high Abbe number) and a large partial dispersion ratio (eg, f). More specifically, the industry requires an optical glass having a higher refractive index (?) and a higher Abbe number (vd) and a larger partial dispersion ratio (eg, f). In particular, the glass disclosed in the patent documents 5 to 13 has a problem that devitrification easily occurs when glass is produced. Since a devitrified glass is produced, it is difficult to fabricate an optical component such as a light that controls, in particular, a visible area. The present invention has been developed in view of the above problems, and an object thereof is to obtain an optical glass having a refractive index (nd) and an Abbe number (Vd) within a desired range and preferably used for correcting chromatic aberration and use thereof. Its lens preform. [Means for Solving the Problem] The inventors of the present invention have conducted intensive experimental research to solve the above problems, and as a result, it has been found that a high refractive index and a low dispersion of glass are achieved by using a B2〇3 component and a La2〇3 component in combination, and a part of glass The dispersion ratio (0 g, the lanthanide system also has a desired relationship with the Abbe number (vd), thereby completing the present invention. In particular, it has also been found that by including the F component, even if the effect of lowering the partial dispersion ratio is included The rare earth element component such as the strong La^3 component, the partial dispersion ratio of the glass (eg 'F) system also has a desired relationship with the Abbe number (five). It is also found that by using the B2〇3 component in combination. With the F component, the low moon culture of the glass is realized and the dispersion ratio of p is also increased, thereby obtaining the desired relationship with the Abbe number (^). Also, it is found that the b2〇3 component and the La2 are also obtained. 〇3 component is used in combination with ai; and F component to achieve high refractive index and low dispersion of glass, and even if the dad 15777l.doc 201231427 contains a rare partial component such as La2〇3 component which has a lower partial dispersion ratio The partial dispersion ratio is also improved. Thus, the desired relationship can be obtained with the Abbe number (Vd), and the liquidus temperature of the glass is increased. Specifically, the present invention provides the following. (1) An optical glass comprising B2〇3 The composition has a refractive index (nd) of 丨.70 or more and an Abbe number (Vd) of 39 or more, and a partial dispersion ratio (0g, F) is satisfied (0g, F)g between the Abbe number (vd) and the Abbe number (vd). (_〇〇〇17〇χ~+〇6375〇) or (〇g 'F)g(-2.〇xl〇-3xVd + 0 6498). (2) Optical glass as in (1) Further, it contains a LasO3 component having a refractive index (nd) of 丨73 or more and an Abbe number (Vd) of 45 or more, and a partial dispersion ratio (0g F) is satisfied (0g, F)g between the Abe number and Ob). (-〇.〇〇i7〇XVd+ 0.63750). (3) Optical glass such as (!), which further contains & 2〇3 component and F component, has an Abbe number (Vd) of 39 or more and less than 52, and a partial dispersion ratio (0g, F) is associated with The number of shells (vd) satisfies the relationship between (eg, F)^(_2 〇xl〇.3xvd+〇. (4) The optical glass of (1), which further contains the F component, in the Abbe number (vd) The xy orthogonal coordinate of the X-axis and the refractive index (1^) is 7 axes, with A(5〇, 1.70)^(60, 1.60) ^C(63, 1.60).Ο(63. 1.70) (A) The optical glass of any of (7) to (4), wherein the total mass of the glass relative to the oxide-converted composition is % by mass, B2〇3 The content of the La203 component is 55% or less, and the content of the La203 component is 55 % or less. (6) The optical glass of (5), which is composed of an oxide equivalent

S 157771.do. 201231427 Total glass quality, containing more than 5.0% La203. (7) The optical glass of (5) or (6), which contains 10.0% or more of the La2〇3 component, based on the total mass of the glass composed of the oxide. (8) The optical glass according to any one of (5) to (7), wherein the content of the La2〇3 component is 5% or less based on the total mass of the glass in terms of oxide conversion. (9) The optical glass according to any one of (1) to (8), wherein the oxide conversion composition further comprises an Al2〇3 component. (10) The optical glass according to any one of (1) to (9), wherein the content of the A12〇3 component is 20.0% or less by mass% based on the total mass of the glass in terms of the oxide conversion composition. (11) The optical glass of (10), wherein the total mass of the glass in terms of the oxide-converted composition is 3% by mass or less and 3% by mass or less of the AI2O3 component. (12) The optical glass according to any one of (1) to (11), wherein the content of the F-component of the oxide-based mass is not less than 3 〇 (four). (13) The optical glass according to (12), wherein the external component is added in an amount of more than 〇%, based on the mass% of the oxide. (10) The optical glass according to (12) or (13), wherein the ratio of the mass of the oxide to the mass of the oxide is not more than 1% by mass. (15) The optical glass according to any one of (1) to (14), wherein the content of the si〇2 component is 40.0% or less by mass% based on the total mass of the glass of the oxide conversion composition. 157771.doc 201231427 (16) The optical glass of (9), wherein the content of the Si〇2 component is 25% by mass or less based on the total mass of the glass in terms of oxide conversion. (17) The optical glass according to (15) or (16), wherein the total mass of the glass relative to the oxide-converted composition is more than % by mass, and the content of the Si 〇 2 component is 25.0% or less. The optical glass of any one of (1) to (17), wherein the mass of the total mass of the glass in terms of oxide conversion is (丨〇8丨〇82〇3) is 4〇. /. the following. (19) The optical glass according to any one of (1) to (18), wherein the Gd2〇3 component is 0 to 40.0% and/or the Y2O3 component is 0% by mass relative to the total mass of the glass in terms of oxide conversion composition. ~20.0% and / or Yb2 〇 3 components 〇 ~ 20.0% and / or LU2 〇 3 components 0 ~ 20.0%. (20) The optical glass of (19), which further comprises the total mass of the glass relative to the oxide-converted composition, in mass%,

Gd2〇3 component 0~40.0% and/or Y2〇3 component 〇20.0% and/or Yb2〇3 component 〇20.0% and/or Lu2〇3 component 〇10.0% of each component. (21) The optical glass according to (19) or (20), which further comprises, in mass%, Gd2〇3 composition 〇30.0% and/or Y2〇3 composition 相对 by mass% relative to the oxide-converted composition. ~20.0% and / or 157771.doc 201231427

The Yb203 component is 220.0% and/or the Lu203 component 〇10.0% of each component. (22) The optical glass according to any one of (1) to (21), wherein the total mass of the glass relative to the oxide-converted composition is, by mass%, the content of Gd2〇3 is 29.5% or less. (A) The optical glass of any one of (1) to (22), wherein the U is selected from La, Gd, Y, Yb, Lu in terms of the total mass of the glass in terms of oxide. The sum of the masses of the above-mentioned groups is 80.0°/〇 or less. (24) The optical glass of (23) wherein the composition of the total mass of the glass relative to the oxide is 1 〇 3 (wherein Ln is selected from the group consisting of La, Gd, γ, Yb, Lu) The mass sum of one or more types is 2% or more. (25) The optical glass according to (23) or (24), wherein the Ln2〇3 component of the total mass of the glass in terms of oxide conversion (wherein Ln is selected from the group consisting of

A group of Gd, Y, Yb, and Lu! The mass sum of the above) is 2% or more and 80.0% or less. (26) The optical glass of any one of (1) to (25), wherein the total mass of the glass is changed with respect to the oxide. The mass of the 3 component (wherein U is selected from the group consisting of La, Gd' Y' Yb, and Lu) is more than 43.0% and 80.0% or less. (27) The glass of the (26), wherein the Ln is selected from the group consisting of La, Gd, γ, and Yb, in which the Ln is selected from the total mass of the glass. The quality of the sum is 5% or less. (28) An optical discontinuity as in (26) or (27), wherein the Ln 203 component of the total mass of the glass consisting of the oxide conversion I5777I.doc - 0. 201231427 (wherein Ln is selected from La,

The mass of one or more of the groups consisting of Gd, Y, and Yb was less than 53.0%. (29) The optical glass according to any one of (1) to (28), wherein the mass of the total mass of the glass relative to the oxide-converted composition and (Gd203 + Yb203) are 26.0% or less. (30) The optical glass according to any one of (1) to (29), wherein a mass ratio Ln2〇3/(Bi203+Ti02+W〇3+Nb205+Ta205) in the oxide-converted composition is 1.7 or more and 25· 0 or less. (31) The optical glass according to any one of (1) to (30), wherein the mass ratio of the oxide-converted composition is Ln2〇3/(Si〇2+B203) is 1.00 or more (wherein Ln is selected from La One or more of the groups consisting of Gd, Y, Yb, and Lu). (32) The optical glass according to any one of (1) to (31) which further comprises, by mass%, based on the total mass of the glass in terms of oxide conversion composition,

Bi2〇3 component 0~10.0% and/or Ti〇2 component 0~15.0% and/or Nb205 component 〇~2〇 〇% of each component. (33) The optical glass according to any one of (1) to (32) further comprising, by mass%, W03 component 〇 15 15 % and/or K 20 component, relative to the total mass of the glass in terms of oxide conversion composition 〇~1〇〇% of each component. The optical glass of any one of (1) to (33), wherein the mass of the total mass of the glass relative to the oxygen exchange is (F+Bi203+Ti〇2+W03+Nb2〇5+K2G^G 1% or more % (4) or less. (35) For the optical surface of (34), the towel is composed of 157771.doc

S -11- 201231427 The total mass of the glass and (F+Bi2〇3+Ti〇2+w〇3+Nb2〇5+K2〇) are 1.0% or more. (36) The optical glass according to any one of (1) to (35), wherein the mass of the total mass of the glass relative to the oxide conversion composition and (Bi2〇3 + Ti〇2 + Wc)3 + Nb205) is 20.0 %the following. (37) The optical glass of (36), wherein the mass of the total mass of the glass relative to the oxide is (Bi2〇3+Ti〇2+w〇3+Nb2〇5^1〇〇% or less. (38) In the optical glass of any one of (1) to (37), the mass ratio F/(F+Bi203+Ti02+W03+Nb205+K20) in the oxide-converted composition is 0.36 or more and 1.00 or less. (39) The optical glass according to any one of (1) to (38), further comprising, by mass%, Zr02 component 〇15.0% and/or Ta205 component 〇~25. 40/.. (40) The optical glass of (39), which further comprises the total mass of the glass relative to the oxide-converted composition, in terms of mass%, Zr02 composition 〇~ΐ5·〇% and/or

Ta205 is composed of 〇15% by weight of each component. (41) The optical glass according to any one of (1) to (40), wherein the mass of the total mass of the glass and the composition (W03 + La203 + Zr02 + Ta205) with respect to the oxide conversion composition is ίο. % or more 6〇 〇% or less. (42) The optical glass of any one of (1) to (41), wherein the mass of the total mass of the glass is converted relative to the oxide (Bi203+Ti〇2+W03 + 157771.doc -12- 201231427

Nb205+Ta205) is more than 〇〇/〇. In the optical glass according to any one of (1) to (42), the total mass of the glass of the composition of the composition is 15.0% or less by mass%. (44) The optical glass of (43), the total mass of the glass, in terms of mass%. The optical glass having a content of the L1 2 〇 component in an oxide-converted composition of 10.0% to (45) as in (44), wherein the total mass of the glass relative to the oxide-converted composition is % by mass% of the Li20 component. 50% or less. (46) The optical glass according to any one of (1) to (45), wherein the mass ratio in the oxide-converted composition (Ta2〇5+Zr〇2+Li2〇)/(F+Bi2〇3+Ti〇2+ W〇3 + _2〇5+;^2〇) is 2.00 or less. (47) The optical glass of any one of (1) to (46), wherein the mass ratio of the oxide exchange composition is (F+Bi2〇3+Ti02+W03+Nb205 + K20)/(Ta2〇5 + Zr02 +Li2〇) is 〇50 or more. (48) Optical glass of (47), wherein the mass ratio of the composition of the oxide is (F+Bi2〇3+Ti〇2+w〇3+Nb2〇5+K2〇)/(Ta2〇5+Zr〇2 +Li2〇) is i 3 or more. (49) The optical glass according to any one of (1) to (4), further comprising, by mass%, Mg0 component 〇 20.0% and/or Ca0 component 〇 ~40.0% and/or Sr0 component 0~40.0% and/or Ba〇 component 〇~55.0% of each component. 157771.doc

S •13· 201231427 (50) The optical glass of (49), which further comprises the total mass of the glass relative to the composition of the oxide, in mass %,

MgO composition 〇~! 〇.〇% and/or CaO component 〇~25.0% and/or SrO component 〇~25.0% and/or BaO component 0~55.0% of each component. (51) The optical glass of (49) or (50), wherein the mass is y with respect to the total mass of the glass in terms of oxide composition. meter,

MgO composition 〇~1〇 〇% and/or CaO component 〇~15〇% and/or SrO component 0~15_0% and/or

BaO composition 〇~25.0%. (50) The optical glass according to any one of (1) to (51), wherein the ruler component is selected from the total mass of the glass in terms of oxide conversion (wherein the ruler is selected from

The sum of the masses of the above-mentioned groups of Mg, Ca, Sr, and yttrium is μ or less. (53) The optical glass of (52), the RO component of the total mass of the glass of the composition of the oxide (in the formula, the anaesthetic is selected from the group consisting of Mg, Ca, and The sum of the masses is below 25%. (54) The optical component of the optical glass of (52) or (53), wherein the ruler is selected from the group consisting of Mg, Ca, Sr, Ba; The quality of the above kind) is less than 2%. (55) The optical glass according to any one of (1) to (54), wherein the MO component contains 157771.doc •14, 201231427 in terms of the amount of f of the total amount of fr of the composition of the oxide in terms of oxide. 20.0% or less. (56) The optical glass of (55), wherein the content of the NkO component is 1% or less based on the mass % of the total mass of the glass in terms of oxide. The optical glass according to any one of (1) to (56), wherein the Rn component is selected from the group consisting of Li, Na, and K with respect to the total mass of the glass in the composition of the oxide. The mass of the above species is less than 25%. (58) The optical glass according to (57), wherein the Rr^O component of the total mass of the glass in terms of oxide conversion (wherein Rn is selected from one or more of the group consisting of 以, 仏, 〖) The mass sum is 15.0% or less. The optical glass according to any one of (1) to (58), wherein the content of the Zn〇 component is 30.0% or less by mass% based on the total mass of the glass of the oxide conversion composition. (60) The optical glass of (59), wherein the total mass of the glass relative to the oxide-converted composition is 5% by mass or less by mass% of the Zn0 component. (61) The optical glass of (59) or (60), wherein the content of the Zn 〇 component in terms of % by mass of the glass in terms of oxide conversion is 15% by weight or less. (62) The optical glass bottle of any one of (1) to (61) which further comprises the total mass of the glass relative to the oxide-converted composition, in mass%,

Ge〇2 component 〇~10.0% and/or p2〇5 component 0~10.0% and/or

Ga2〇3 composition 〇~10.0% and/or

157771.doc S 201231427

Te02 composition 0~10.0°/. And/or Sn02 component 0 to 5.0% and/or Sb203 component 0 to 1.0% of each component. (63) The optical glass of (62), wherein the total mass of the glass relative to the oxide-converted composition is 0-10.0% by mass of the Ge02 component and/or 0 to 10.0% of the P2O5 component and/or

Ga203 component 0~10.0% and/or Te02 component 0~10.0% and/or

Sn02 component 0~1.0% and/or Sb203 component 〇~1.〇%. The optical glass according to any one of (1) to (63), which has a refractive index (nd) of 157 or more and an Abbe number (vd) of 45 or more. (65) The optical glass of any one of (1) to (6), wherein the Abbe number is between Svd2-100xnd+220 and the refractive index (nd). (66) as in (1) to (65) The optical glass of any one of (65), wherein the Abbe number (Vd) is related to a refractive index (η < 满 between Svd2-125xnd + 265. () a preformed body comprising The optical glass of any one of (1) to (66). (68) An optical element produced by extrusion molding a preformed material such as (67). (69) An optical element, The optical glass of any one of (1) to (66) is used as a base material. (7〇) is an optical machine comprising an optical component such as (68) or (69). 15777l.doc 201231427 [Effect of the Invention] According to the present invention, an optical glass having a refractive index (...) and an Abbe number within a desired range and preferably used for correcting chromatic aberration, a preform using the same, and optical can be obtained. [Embodiment] The optical glass of the present invention contains a b2〇3 component, and a partial dispersion ratio (0g, F) is satisfied (0g, F)g between the Abbe number (vd) (_〇〇) 17〇XVd+ 0.63750) or (eg ' F)g (-2.〇xl〇_3XVd+〇6498). The partial dispersion ratio (0g, F) satisfies the specific relationship with the Abbe number (Vd). Thereby, the chromatic aberration of the optical element formed by the optical glass is lowered. Therefore, the refractive index (nd) and the Abbe number (Vd) can be obtained within a desired range and can be preferably used for correcting chromatic aberration. An optical glass, a preform using the same, and an optical element. In particular, the first optical glass (hereinafter referred to as a first optical glass) contains a B2〇3 component and a La2〇3 component, and has a crucible 73. The above refractive index (nd) and the Abbe number (Vd) of 45 or more, the partial dispersion ratio (0g, F) is satisfied with the Abbe number (%) (eg, F)g (_〇〇〇17 〇xvd+〇6375〇). In particular, in the first optical glass, the b2〇3 component is included

The La^3 component, whereby the refractive index of the glass is increased and the dispersion is reduced. Further, the partial dispersion ratio (eg 'F) satisfies a specific relationship with the Abbe number (Vd), whereby the chromatic aberration of the optical element formed of the optical glass is lowered. Therefore, an optical glass having a refractive index (nd) and an Abbe number (Vd) in the range of f and having less coloration and preferably used for correcting chromatic aberration, a preform using the same, and optical can be obtained. element. 157771.doc 5 201231427 Further, the optical glass of the second embodiment (hereinafter referred to as a second optical glass) contains a B2〇3 component, a La2〇3 component, and an F component, and has a refractive index of 1⁄7 or more. Nd) and above the Abe number (vd) of 52, the partial dispersion ratio (Gg, F) is satisfied with the Abbe number (Vd), F)g (_2 〇χ1()·3χ vd + 0.6498) relationship. In particular, in the second optical glass, the B2〇3 component and the La2〇3 component are contained, whereby the refractive index of the glass is increased and the dispersion is reduced, and the transparency to visible light is also improved. In addition, the F component is contained, and even if the rare earth element component such as the LhO3 component having a strong partial dispersion ratio is contained, the partial dispersion ratio (0g, F) is improved, whereby the color image of the optical element formed of the optical glass is formed. The difference is falling. Therefore, an optical glass in which the refractive index (heart) and the Abbe number (vd) are in a desired range and which is less colored and can be preferably used for correcting chromatic aberration can be obtained. Further, the optical glass of the third embodiment (hereinafter, referred to as a third optical glass) contains bismuth; a component and an F component, and has an Abbe number (%) as a 乂 axis and a refractive index (nd) as a y-axis. In the xy orthogonal coordinates, there are Abbe numbers and refractions in the range surrounded by 4 points of a(5(), 1 7〇), B(60 1.60), C(63 ' 1.60), D(63, 1.70). The rate, the partial dispersion ratio (0g, F) is related to the relationship between (Gg 'F)g-〇.〇〇17〇XVd+〇6375 with the Abbe number...). In particular, the first light 4 · glass $, and the use of the bismuth component and the F component, thereby achieving a low knife economy, and the partial dispersion ratio is also improved, thereby being between the Abbe number and d) Get the relationship you need. Therefore, an optical glass having a refractive index...) and an Abbe number )d) which is in the range of the above and which can be preferably used for correcting chromatic aberration, a preform using the same, and an optical element can be obtained. The fourth real thin optical glass (hereinafter, set as the fourth optical glass 157771.doc

-18- 201231427 Glass) is based on quality. The composition contains 5.0 to 55.0% of the 1〇3 component, 1〇〇~55〇% of the La2〇3 component, and further includes the barium 2^ component and the F component. In particular, in the fourth optical glass, the b2〇3 component and the LhO3 component are contained within a specific content range, whereby the refractive index of the glass is increased and the dispersion is reduced, and the transparency to the visible light is improved. In addition, the Ah 〇 3 component and the F component are used in combination with the bismuth component and the component, and the partial dispersion ratio (0g is improved even if the rare earth element component such as the La"3 component having a strong partial dispersion ratio is contained. The temperature of the liquid phase of the glass is increased. Therefore, the refractive index (nd) and the Abbe number (vd) are in the range of f and can be preferably used for correcting chromatic aberration and having high devitrification resistance. In the following, the embodiment of the optical glass of the present invention will be described in detail. However, the present invention is limited to the following embodiments, and may be appropriately modified and modified within the scope of the present invention. The description of the components is omitted as appropriate. However, the purpose of the invention is not limited. [Glass component] Hereinafter, the composition range of each component constituting the optical glass of the present invention will be described. In the present specification, the content of each component is not specifically described. In the case of ::form, all are expressed as mass % of the total mass of the glass in terms of oxide composition. Here, the term "oxide conversion composition" means when used as a hypothesis When the oxide, the composite chain, and the metal sharpening of the raw material of the glass component are all decomposed and converted into an oxide during the melting, the total mass of the produced oxide is set to 1% by mass. The composition of each component contained in the glass. <About required components, arbitrary components>

S I5777I.doc •19·201231427 The B2〇3 component is a component that forms a network structure inside the glass and promotes stable glass formation. In particular, the content of the B2〇3 component is set to 50% or more, thereby making the glass It is difficult to get rid of, and it is easy to obtain stable glass. On the other hand, the content of the Βζ〇3 component is set to 55,0% or less, whereby the desired refractive index and dispersibility can be easily obtained. Therefore, the lower limit of the content of the cerium component relative to the total mass of the glass in terms of oxide is preferably 5 〇〇 / 〇, more preferably 8.0%, most preferably 10.0%, and still more preferably 13 〇 %. The best is 15.0%. On the other hand, it is preferable to set the content of the B2〇3 component to be more preferably 50.0%, more preferably 45% by weight, still more preferably 55.0%, and preferably 4%. 35.0%. In particular, in the optical glass of the present invention, the upper limit of the content of the B2〇3 component may be set to 3〇〇%βΒ2〇3 component, for example, Η3Β〇3 ', Na2B4〇7 Cong 2〇, 2 may be used. It is contained in the glass as a raw material.

The LhO3 component is a component that reduces the refractive index of the glass and reduces the dispersion. In particular, when the content of the LhO3 component is 55.5% or less, the phase separation of the glass is suppressed, and when the glass is produced, the glass is hard to devitrify. Therefore, the upper limit of the content of the "component of the Ο3 component" is preferably 55.0%, more preferably 54.%, more preferably 53.%, and further preferably It is 52%, more preferably 5%, and most preferably 45., 〇%. Further, the lower limit of the content of the La2〇3 component is suitable for obtaining a glass having a light-drying property as appropriate. It is set, but by setting the content of the component to 5.0% or more, it is possible to easily obtain a glass having a desired higher refractive index and a higher Abbe number and having a higher transmittance to visible light. The lower limit of the content of the La2〇3 component is preferably set to 5 〇%, more preferably 157771.d〇c

-20- 201231427 is 10·0%, further preferably more than 120%, further preferably 13%, and further preferably 15.0%. The lower limit of the content of the La2〇3 component may be 2〇.〇%, or the lower limit may be 25.0%. For the La2〇3 component, for example, WO3, La(N〇3)rXH2(R) (an arbitrary number of x), or the like can be used as a raw material, and the F component can be used to increase the partial dispersion ratio of the glass, and the glass can be reduced. (Tg) component. In particular, the content of the component is set to be below o o%, whereby the stability of the glass can be improved and it is difficult to devitrify. Therefore, the upper limit of the content of the F component in terms of the ratio with respect to the oxide reference mass is preferably 30.0%, more preferably 25% by weight, still more preferably 20.0%' is preferably 15.0%. In particular, the content of the F component in the third optical glass may be 10.0% or less. Furthermore, the optical glass of the present invention has a ratio of optical glass to the optical glass of the present invention, but by the W component, an optical glass having a higher partial dispersion ratio and less coloration can be obtained. The lower limit of the content of the F component in addition to the ratio is set to be more than 〇, more preferably 〇.1%, more preferably more than 〇.5%, and thus

157771.doc 201231427 Furthermore, the content of the F component in the present specification assumes that the cationic components constituting the glass all form an oxide which is bonded to the oxygen which is just a charge balance amount and which is formed by the oxides. The mass is set to 100% ' and the mass of the F component is expressed in mass % (the proportional mass is added to the vapor reference mass. /0).

The Al2〇3 component is a component which is easy to form a stable glass and is an optional component of the glass of the present invention. In particular, the content of the Ai2〇3 component is set to 20. (4) τ, whereby the decrease in the Abbe number of the glass can be suppressed. Therefore, the upper limit of the content of the component from the total mass of the glass of the oxide-converted composition is preferably 20%, more preferably 15%, still more preferably 10.0%. . The upper limit of the content of the Magic 2〇3 component may be preferably 8.0%', more preferably 5% by weight, and most preferably 2% by weight. Here, the Α!2〇3 component may not be included, but particularly in the fourth optical glass, the decrease in the Abbe number of the glass can be suppressed by including the Αι2〇3 component. Therefore, the lower limit of the content of the Al2〇3 component relative to the total mass of the glass in terms of the oxide conversion composition is more preferably more than 0%', more preferably 0.1%, still more preferably 0.5%, and more preferably 1.0. % ' is further preferably more than 3 %, and most preferably more than 3 4%. The 乂2〇3 component can be contained in the glass, for example, using Μ"3, AK〇H)3, Alh or the like as a raw material. In particular, in the fourth optical glass, the ratio of the content of the component 〇2〇3 to the content of the f component = is preferably greater than 〇 and 15 〇 or less. By setting the ratio within a specific range, thereby improving the stability of the glass, it is possible to obtain a glass which is more resistant to devitrification. Therefore, the lower limit of the mass ratio A12〇3/f of the oxide-converted composition is preferably larger than 〇, more preferably 〇, and most preferably 〇3. The other party 157771.d〇, •22-201231427 sets the upper limit of the σ海 ratio to preferably i5 〇, more preferably 1, more preferably 5.0, still more preferably 4 〇, and most preferably 3.4. In addition, the content of the content of the F component in the ratio of the content of the content of the F component is in the ratio of the ratio of the ratio of the content of the alloy to the ratio of the ratio of the content of the alloy, and the content of the Al2Q3 component is the total mass of the glass in terms of the composition of the oxide. The content.

The Si〇2 component is a component that promotes stable glass formation and suppresses devitrification (production of crystallized matter) in the production of glass, and is an arbitrary forming tool in the optical glass of the present invention, in particular, the content of the S1〇2 component is set to 40.0% or less, whereby the 31〇2 component is easily dissolved in the molten glass, and dissolution at a high temperature can be avoided. The upper limit of the content of the 〇2 component relative to the total mass of the glass in terms of the oxide conversion composition is preferably 4 G.G%, more preferably, still more preferably less than 28.0%, and still more preferably 25 (). %, further preferably less than 25%, more preferably 24.0%, still more preferably 2%, 胄%, and less than 20.0%. In particular, in the first, second, and fourth optical glasses, the upper limit of the content of the si 〇 2 component may be set to 15 〇 %, and the upper limit may be set to 10.0%. Further, even if the Si 2 component is not contained, a glass having a desired higher partial dispersion ratio can be obtained, but by containing the SiO 2 component, the devitrification resistance of the glass can be improved. Therefore, the lower limit of the content of the Si〇2 component relative to the total mass of the oxide-converted group is preferably more than 〇%, preferably 0.1%, more preferably 0.5%, still more preferably 1.0%. . In particular, in the second optical glass, the content of the component may be H or may be more than 5.0%. The Si〇2 component can be contained in the glass, for example, using (10), K^SiF6, Na and SiF6% as raw materials. In particular, in the fourth optical glass, the composition of the Si〇2 component and the B2〇3 component

S 157771.doc 201231427 Quantity and preferably 40.0% diced. Under the test, the refractive index of the glass is suppressed, so that an optical glass having a desired high refractive index can be obtained. Therefore, the mass of the total mass of the glass converted to the composition of the emulsion is set to (the upper limit of the addition is preferably set to %, more preferably μ 〇% is preferably 32. Further, the stability is higher. And from the viewpoint of the glass having a high resistance to devitrification, the amount of 'f and _2+B2〇3) is preferably 5.0%, more preferably 1〇.〇%, and most preferably 15 〇%. The composition of 〇33 is to increase the refractive index of the glass and to reduce the component of dispersion. In particular, the content of the Gd2〇3 component is set to 4% by weight or less, whereby the phase separation of the glass, J', makes the glass difficult to devitrify when the glass is produced. Therefore, the upper limit of the content of the G component relative to the total mass of the glass in terms of the oxide-converted composition is preferably preferably G%, more preferably 35 G%, more preferably 30.0%, most preferably 29.5%. In particular, in the optical surface of the 苐三三, the content of the Gd component may be preferably less than (four), more preferably less than 2, and most 20.0%. q If you don't want to use it, even if you don't include the Gd2〇3 component, you can get the glass with the desired higher partial dispersion ratio. However, you can easily obtain the desired refractive index by including 〇ι% or more. Dispersibility. Therefore, the lower limit of the content of the % 〇 3 component of the total mass of the glass in terms of the oxide conversion composition is preferably, more preferably, red Q%, and the heart is preferably 2 birds. In the first and fourth optical glasses, the lower limit of the content of the Gd2〇3 component may be set to 5·0%', and the lower limit may be set to 7, 〇%. (5) Component system For example, Gd2〇3, GdF3, or the like can be used as a raw material and contained in glass. ’, 157771.doc •24- 201231427 Υ2〇3, Yb>2〇3 and Lu2〇3 are components that increase the refractive index of the glass and reduce the dispersion. Here, Y2〇3 component, Yb2〇3 component or

The content of the Lu2〇3 component is set to 20.0% or less, whereby the glass is hard to be devitrified. In particular, when the content of the Yb>2〇3 component is 10.0% or less, absorption on the long wavelength side of the glass (near the wavelength of 1 〇〇〇 nm) is less likely to occur, so that the glass can be improved in the infrared ray. Therefore, the upper limit of the content of the Y2〇3 component and the Yt>2〇3 component of the total mass of the glass in terms of the oxide conversion composition is preferably 20.0%, more preferably 15.0%, still more preferably 1〇〇. %, further preferably 8.0%, further preferably 5_0% 'best 4.0%. Further, the upper limit of the content of the Lu 2 〇 3 component based on the total mass of the glass in terms of oxide conversion is preferably 20.0%, more preferably 15.0%, still more preferably 10% '% and further preferably 8.0. %, further preferably 5 〇%, most preferably 3.0%. In particular, from the viewpoint of improving the resistance of the glass to infrared rays, the content of the Yb2〇3 component relative to the total mass of the glass in terms of oxide composition is preferably less than 3.0%, and most preferably not i 〇%. ΙΟ; ingredients, bamboo 2〇3 components and lU2〇3 components can be used, for example, γρ3,

Yb203, lU2〇3, etc. are contained in the glass as a raw material. In the optical glass of the present invention, the 'Ln2〇3 component (wherein, (4) is selected from

The content of the content of the group consisting of La, Gd, γ, Yb, and Lu is equal to or less than 8 G.G%. Thereby, the glass when the glass is produced can be reduced: devitrification. The mass and the upper limit of the content of the 丄^2〇3 component of the total mass of the glass yttrium having an oxide conversion composition are preferably 8 〇 g%, and more H Μ is. In particular, in the third optical glass, the mass and the upper limit of the content of the Ln2〇3 component may be preferably 63.5%, more preferably 60.0%, and further preferably 157771.doc -25·201231427. The best is 55〇%, and the best is less than 5〇.〇%. Further, the lower limit of the total content of the Ln2〇3 component is appropriately selected within the range of the optical glass in which the desired characteristics can be obtained, but is, for example, set to more than 1% by mass, whereby the desired higher refractive index can be easily obtained. Rate and Abbe number, reduce coloration, and reduce photoelastic constant. In particular, in the optical glass of the present invention, even if a large amount of rare earth is contained, the partial dispersion ratio is hard to be lowered, so that a higher partial dispersion ratio and a higher refractive index and Abbe number can be easily achieved. Therefore, the mass and the lower limit of the content of the Ln2〇3 component relative to the total mass of the glass in the oxide conversion composition are preferably more than 1% by weight, more preferably more than 15.0/〇, and thus the car is good. It is more than 16%, more preferably 〇%, and most preferably more than 20%%. In particular, in the first, second, and fourth optical glasses, the mass and the lower limit of the content of the Ln2〇3 component may be preferably 30.0%, more preferably 4% by weight, and further preferably. It is more than 43%, more preferably 45.0%, still more preferably 5%, and most preferably 55 %. In particular, in the third optical glass, the sum of the component of the GAO; and the component of Yb2〇3 is preferably 26.0% or less. Thereby, it is possible to suppress the use of the Gd2〇3 component and the Yb2〇3 component which have a function of increasing the refractive index, so that the partial dispersion ratio is improved, and the desired refractive index and dispersion can be easily obtained. Therefore, the mass of the total mass of the glass and the upper limit of (Gd2〇3+Yb2〇3) with respect to the composition of the oxide are again good for 26 〇〇/. More preferably, it is 23 〇0/❶, and further preferably 〇%, and most preferably 1 5.0. /. . Further, in the optical glass of the present invention, the content of the 'LhO3' is good for the mass and the quality of the (9), +, Ding, 训, +, and + (6) 157771.doc • 26-201231427 25.0 or less. Therefore, the total content of the Lb2〇3 of the Abbe number is increased within a specific range with respect to the total content of the component of the Abbe number, the addition of the 2 component, the W〇3 component, the Nb2〇5 component, and the Ta2〇5 component. Therefore, it is possible to obtain the required Abbe number, and even have a desired relationship between the partial dispersion ratio and the Abbe number. Therefore, the lower limit of the mass 2 Li^OABhOeTiOdWC^+Nl^C^+Tae5) in the oxide-converted composition is preferably 1·7', more preferably 3·〇', and even more preferably 5.G'. The upper limit is preferably set to 25.0, more preferably 20.0, and most preferably i6.8. Further, in the fourth fresh glass, the content of the component 'Ln2〇3 (wherein, selected from the group consisting of Gd, Y, Yb, and Lu) is the ratio of the component to the component and the mass of the component. Good for more than 1〇〇. When the ratio is (4), the refractive index is improved even if the Al2?3 component is contained, so that an optical glass having a high partial dispersion ratio and having both glass stability and high refractive index can be obtained. Therefore, the lower limit of the mass ratio Ln203/(Si02+B2〇3) of the oxide conversion composition is preferably i (8), and more preferably the red 25' is preferably L40. On the other hand, the upper limit of the rate of (4) is not particularly limited as long as it can obtain stable glass. However, for example, when it exceeds (4), it is presumed that there is a possibility that devitrification is likely to occur. For the &, the oxide is converted, and the upper limit of the mass ratio Ln2〇3/(Si〇2+B2〇3) is preferably ι〇〇〇, = U0, and the best is 5 Qin Yuyi Among the components, the La2〇3 component is/in order to improve the stability of the glass, so that it is more preferable to obtain La203/(si02+B2〇3 from the viewpoint of obtaining a glass having particularly high devitrification resistance. The ratio of the ratio is set to the above range... In terms of the glass which is more resistant to devitrification, the mass ratio of the oxide conversion composition can also be obtained.

S 157771‘doc -27· 201231427

The upper limit of La2〇3/B2〇3 is preferably 1 〇 〇〇, more preferably 5 〇〇, and still more preferably 3.5 G' and further preferably 23 (), and most preferably less than 2 Å.

The Bi2〇3 component is a component which increases the refractive index of the glass and increases the refractive index 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, the content of the Bi203 component was set to 10.0/. In the following, it is difficult to deteriorate the light transmittance of visible short wavelengths (below 5 Å nm). Therefore, the upper limit of the content of the Bi2〇3 component of the glass total S of the oxide-converted composition is preferably 1% ,%, more preferably 8.0%. 'Best is 5.0. /. . The 2〇3 component can be contained in the glass, for example, by using Bi2〇3 or the like as a raw material. The Τι〇2 component is a component which increases the refractive index of the glass and which increases the refractive index of the mother and disperses and increases the chemical durability of the glass, and is an optional component in the optical glass of the present invention. In particular, by setting the content of the Ti 2 component to 15.0 Å/〇 or less, it is easy to obtain a desired high Abbe number, and it is difficult to achieve a light transmittance of a short wavelength (below 500 nm). deterioration. Therefore, the upper limit of the content of the butyl sulfonium 2 component relative to the total mass of the glass in terms of the oxide conversion composition is preferably 15% by weight, more preferably 12% by weight, still more preferably 10.0%, and further preferably 8〇%, further preferably 7〇%, and most preferably 5.0%. The Ti 2 component can be contained in the glass, for example, using Ti 2 or the like as a raw material. ,

The NhO5 component is a component which increases the refractive index of the glass and increases the refractive index and dispersion of the glass and improves the chemical durability of the glass, and is an optional component in the optical glass of the present invention. In particular, the content of the 〇5 component is set to 20.0% or less, whereby the desired higher Abe 157771.doc -28-201231427 number can be easily obtained. Therefore, the upper limit of the content of the Nb2〇5 component relative to the total mass of the glass in the oxide conversion composition is preferably 20% by weight, more preferably ΐ5·0/〇' is preferably 10.0 Å/〇. The Nb2〇5 component can be contained in the glass, for example, using Nb2〇5 or the like as a raw material. The WO3 component is a component which increases the refractive index of the glass and increases the refractive index and dispersion of the glass and improves the chemical durability of the glass, and is an optional component in the optical glass of the present invention. In particular, the content of the component is set to be 15.0% or less, whereby the desired higher Abbe number can be easily obtained, and the light transmittance of the visible short wavelength (below 5 nm) is hard to be deteriorated. The upper limit of the S? with respect to the total mass of the glass of the oxide-converted composition is preferably 15%, more preferably 12, still more preferably 10.0%, still more preferably 8%. The best is 5 〇%. Further, even if the W03 component is not included, an optical glass having a desired higher partial dispersion ratio can be obtained. However, by setting the content of the w〇3 component to be higher, the partial dispersion ratio of the glass can be increased. A glass having a desired higher partial dispersion ratio is obtained. Therefore, the lower limit of the content of the W〇3 component of the total mass of the glass in terms of the oxide-converted composition is preferably, and more preferably 3%. The w〇3 component can be contained in the glass, for example, using w〇3 or the like as a raw material. The K2 bismuth component is a component which increases the component ratio of the glass in a stepwise manner and improves the (tetra) property of the glass, and is an optional component in the optical glass of the present invention. In particular, when the summer content of κ2〇忐8+ a θ is set to 10.0% or less, the refractive index of the glass is hard to be lowered, and the enthalpy of the glass is increased to make it difficult to produce. Therefore, the upper limit of the content of the κ ζ 成分 component of the total amount of the granules of the oxide-converted composition is preferably ι 〇〇 %, more preferably 8.0% 'best 5.0. %. The κ20 component can be contained in the glass, for example, using K2C〇3, KN〇3, KF, KHF2, K2SiF6 or the like as a raw material. In the optical glass of the present invention, one or more selected from the group consisting of the F component, the Bi2〇3 component, the Tih component, the WO component, the Nth component, and the palpitant component are preferably 〇i% or more. . The sum is set to 〇 1% or more, whereby it is necessary to include a component having a high partial dispersion ratio of S, so that a desired higher partial dispersion ratio can be easily obtained. x, because the partial dispersion ratio of the glass is high, the partial dispersion ratio can have a desired relationship with the Abbe number. Therefore, the lower limit of the content of the components relative to the mass of the oxide-converted composition is preferably 0.1%, more preferably 丨〇%, still more preferably 3.0%, and still more preferably 4. %, further preferably 5 %, further preferably 6.2%, most preferably 8. %. Further, the content and the upper limit of the components such as hydrazine are not particularly limited as long as a stable glass can be obtained. However, for example, when it exceeds 60.0%, it is presumed that there is a possibility that devitrification is likely to occur. Therefore, the content and the upper limit of the components relative to the mass of the oxide-converted composition are preferably 60.0%, more preferably 50.0%, still more preferably 4% by weight. In particular, in the second and third optical glasses, the content and the upper limit of the components relative to the mass of the oxide-converted composition may be preferably 30.%%, more preferably 25.0%, more preferably Good is 20_0%, best is 15%. In addition, in the content and content, the content of the F component means the content in addition to the oxide-based mass, and the 2〇3 component 'Ti〇2 component' j component, Nb2〇5 component, and Re component. The content refers to the content of the total mass of the glass relative to the oxide conversion. 157771.doc -30- 201231427 Among these components, the κβ component has a function of lowering the refractive index, and therefore, from the viewpoint of obtaining a glass having a particularly high refractive index, it is preferable to contain a component selected from the F component and Bi2〇3. One or more of the group consisting of a component, a Ti〇2 component, a w〇3 component, and a 〇5 component. Further, since the Nb2〇5 component is more effective in lowering the Abbe number, it is preferable to include a glass having a particularly high Abbe number, and it is preferable to contain a component selected from the F component, the 2〇3 component, and the Ti〇. One or more of the group consisting of the two components, the w〇3 component, and the K2〇 component. Further, since the Bi2〇3 component 'Ti〇2 component and the W〇3 component have a strong effect of coloring the glass, it is preferable to include a component selected from the F component from the viewpoint of obtaining a glass having a particularly small coloration. More than one of the group consisting of the Nb2〇5 component and the K2〇 component. Therefore, from the viewpoint of obtaining a glass having a higher partial dispersion ratio and a higher refractive index and Abbe number and less coloration, it is preferred to increase the content of the components particularly in the F component. In the optical glass of the present invention, the Bi2〇3 component of the components,

The content of the Ti〇2 component, the w〇3 component and the Nb2〇5 component is preferably 2〇.〇% or less. Thereby, the component which is improved in dispersion is reduced, so that the glass having the desired dispersion can be easily obtained. Further, since the decrease in the stability of the glass caused by the excessive inclusion of the components is suppressed, the resistance to devitrification of the glass can be further improved. Therefore, the upper limit of the mass of the glass and the upper limit of (Bi203 + Ti02 + W〇3 + Nb2 〇 5) with respect to the oxide-converted composition is preferably 2% by weight, more preferably 15.0%, and most preferably 1〇〇%. In particular, the mass and the upper limit in the third optical glass may be set to 8 〇%, and the upper limit may be set to 5 〇%. Further, from the viewpoint of obtaining a glass which is particularly small in dispersion, the mass sum may be set to less than 0.5%. On the other hand, even if it does not contain any such

S 157771.doc 201231427 points 'Optical glass with a desired higher partial dispersion ratio can also be obtained, but the partial dispersion ratio of the glass can be easily obtained by setting the mass sum of the components to 01% or more. The glass having the desired higher partial dispersion ratio... can also be the lower limit of the mass and (Bi2o3+Ti〇2+W()3+Nb2〇5) from the viewpoint of obtaining a higher partial dispersion ratio. It is preferably set to 0.1%, more preferably 0.5. /. Further preferably 〇 8%. Especially in the third optical glass, the content of the F component is opposite to the f component,

The content of the Bl2〇3 component, the Ti〇2 component, the W〇3 component, the 〇5 component, and the Κ2〇 component is preferably 36 or more. In particular, the ratio is set to 0.36 or more. Thus, a transparent glass having a desired partial dispersion ratio can be obtained by containing a large amount of a component which increases the partial dispersion ratio and which is less colored. Therefore, the lower limit of the mass ratio F/(F+Bi2〇3+Ti such as W〇3+Nb2Q5+K2〇) in the oxide-converted composition is preferably Q36, more preferably (4), still more preferably 0.5. 0. In addition, in the case of the % Zeng County, Dan has a better than 1.00, but in terms of the desire to obtain a more stable glass, it can be less than 100.

The Zr〇2 component is a component which increases the refractive index of the glass and improves the resistance to breakage in the production of glass, and is an optional component in the optical glass of the present invention. In particular, the content of the ZrO 2 component is set to 15 (10), whereby the decrease in the partial dispersion ratio of the glass can be suppressed. X, the content of the ton component is set to 〇% or less, thereby suppressing the decrease in the glassy Abbe number and avoiding the melting at the high temperature at the time of glass production, which can reduce the energy loss at the time of glass production. Therefore, the upper limit of the content of the core component of the total mass of the glass in terms of the oxide conversion composition is preferably 15.0%, more preferably 1% by weight, still more preferably 8·0/. Further preferably, it is 7.0%, more preferably 5.0%, and most preferably it is less than 157771.doc -32 - 201231427 4.0%. Further, even if the Zr 〇 2 component is not contained, a glass having desired optical characteristics can be obtained. However, by setting the content of the Zr 〇 2 component to 〇 1% or more, the devitrification resistance of the glass can be improved. Therefore, when the Zr〇2 component is contained, the lower limit of the yttrium content of the Zr〇2 component relative to the total mass of the glass in the oxide conversion composition is preferably 01%, more preferably 〇5%, and further Good is 1.0%. The Zr 2 component can be contained in the glass, for example, using Zr 2 , ZrF 4 or the like as a raw material.

The Ta2〇5 component is a component which increases the refractive index of the glass and stabilizes the glass, and is an optional component in the optical glass of the present invention. Especially, will

The content of the TkO5 component is set to be less than or equal to 25.5%, thereby suppressing a decrease in the knife-to-knife ratio of the glass. Further, the content of the τ&2〇5 component is set to 25 or less, thereby reducing the material cost of the glass, and It can avoid melting at high temperatures and reduce energy loss during glass manufacturing. Therefore, the upper limit of the content of the TkO5 component relative to the total mass of the glass in the oxide conversion composition is preferably 25.0%, more preferably less than 165%, still more preferably Η(iv), and still more preferably 1 〇· 〇%, the best is 5.0%. The Ta2〇5 component can be contained, for example, as a raw material in the glass. In the optical glass of the present invention, the content of the W〇3 component, the La2〇3 component, the ton component, and the Ta2〇5 is preferably 10.0% or more. The sum is 2 1 to allow the above to reduce the color of the glass, and the refractive index can be further increased. Therefore, the content and the lower limit of the components relative to the mass of the oxide-converted composition are preferably set to 10. ()%, better for moving%, the best is 3. On the other hand, the content and the upper limit of the components are not particularly limited as long as a stable glass is obtained, but for example, super

S 157771.doc -33- 201231427 When 65.0% passed, it is speculated that there is a possibility of devitrification. Therefore, the content of the components relative to the mass of the oxide-converted composition is preferably 65.0%, more preferably 6 〇.%, and still more preferably 5% 5%. In particular, in the second optical glass, the content of the group consisting of the % 〇 3 component, the Ti 0 component, the (4) 3 component, the Nb 2 〇 5 component, and the Ta 2 〇 5 component is preferably more than 〇%. Thereby, since the glass is small, the optical glass having the Abbe number of the desired range can be easily obtained: Therefore, it is preferable to set the content and the lower limit of the mass (four) and the like with respect to the composition of the oxide. 〇%, $ 2. %. On the other hand, it is more preferable that the components are the most stable glass, and the upper limit and the upper limit are particularly limited as long as they are available, but for example, the possibility is more than 25 %. Therefore, the content of the ingredients and the upper limit of the ingredients will be set to be more than 25.0/. ‘More preferably 15.〇%, the best is (7) Tour”

The Li2〇 component improves any component in the glass. In particular, the t t component is the optical device of the present invention, whereby the portion of the glass is suppressed:;:. : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : : The upper limit of the content of the component for the conversion of the oxide::= is preferably set to (4) of the total mass of the glass to be preferably 8%. Further preferably 5:, more preferably. Further, it is more preferably 4.0 /. ' Further preferably 157771.d〇<-34-201231427 3.0%, further preferably less than 3.0%, further preferably 2.3%. Especially, it is easily obtained. The content of the LhO component may be 0.5% or less, or may be 0.4% or less, or may be less than 0.1%, from the viewpoint of an optical glass having a higher partial dispersion ratio. The component may be contained in glass, for example, using LhCO3, LiN〇3, LiF or the like as a raw material. In the optical glass of the present invention, the content of the 'Ta2〇5 component, the Zr02 component, and the Li2〇 component and the F component are The content of BbO3 component, Ti〇2 component, W〇3 component, Nb>2〇5 component, and κ:2〇 component is preferably 2 〇〇 or less. The content of the component having a low partial dispersion ratio is less than that of the component having the effect of the direction-to-part dispersion ratio, so that a glass having a higher partial dispersion ratio can be obtained. Therefore, the mass-to-star ratio (Ta2) in the composition of the oxide is obtained.上限5+Zr02+Li2〇)/(F+Bi2〇3 + Ti〇2 + W03+Nb2〇5+K2〇) The upper limit is preferably set to 2. 〇〇' is preferably 1.40, more preferably 1 〇〇, the optimum is 0.80. In addition, the mass ratio may be 〇, but by setting the mass ratio to 0·10 or more, the devitrification resistance of the glass can be further improved. The lower limit of the mass ratio (Ta205+zr02+Li20)/(F+Bi203+Ti02+W03+Nb205+K20) in the composition is preferably 〇·1〇, more preferably 〇2〇, and most preferably 0.30. In the optical glass of the present invention, the mass of the (F+Bi2〇3 + Ti02 + W03 + Nb205+K20) and the ratio of the mass (Ta2〇5+Zr〇2+Li2〇) are preferably 0.50 or more. Therefore, since the content of the component of the partial dispersion ratio is more than the content of the component which greatly reduces the partial dispersion ratio, even if more rare earths are added, the desired higher portion can be easily obtained. San ratio. That is,

S 157771.doc -35- 201231427 It is easy to balance the higher partial dispersion ratio with the higher Abbe number. Therefore, the lower limit of the mass ratio (F+Bi2〇3+Ti()2+WQ3+Nb2C)5+K20)/(Ta205+Zr〇2+Li2〇) in the oxide-converted composition is preferably 〇 5〇, more preferably 1.00, still more preferably 1.32, and still more preferably 丨7〇. In particular, in the first optical glass, the ratio of the content may be preferably 13 or more preferably 1.5 Å to 2. G. On the other hand, the upper limit of the ratio of the content is not particularly limited and may be infinite (i.e., TaedZrOdUWi%), but the ratio may also be 1 观点 from the viewpoint of further improving the stability of the glass. the following.

The MgO component, the Ca 〇 component, the Sr 〇 component, and the Ba 〇 component are components which improve the meltability of the glass and improve the devitrification resistance, and are optional components of the optical glass of the present invention, in particular, the content of the Mg 〇 component is set. When the content of the CaO component or the Sr〇 component is 4% by weight or less, or the content of the BaO component is 55% by weight or less, the refractive index of the glass is hardly lowered. Therefore, the upper limit of the content of the MgO component relative to the total mass of the glass in the oxide conversion composition is preferably 2% by weight, more preferably 15.0%, still more preferably 1% by weight, still more preferably 8 〇%, the best is 5.0/〇. Further, the upper limit of the total amount of ca 相对 of the total amount of the glass in terms of the oxide conversion composition is preferably 4 〇 〇 %, more preferably 3 〇 〇 %, and further, the car is 25.0. /. Further, it is preferably 2% by mole, more preferably 15% by weight, still more preferably 12.0%, still more preferably 1% by weight, most preferably less than 1% by weight. Further, the upper limit of 3 of the Sr 〇 component of the total mass of the glass in terms of the oxide conversion composition is preferably 40% by weight, more preferably 30.0%, still more preferably 25.0%' and further preferably 2 〇〇. %, and thus preferably less than 16%, and further 157771.doc

Further, the upper limit of the content of the Sr0 component is more preferably 12.0%, still more preferably 10.0%. Further, the upper limit of the content of the Ba0 component based on the total mass of the glass in terms of the oxide conversion composition is preferably 55.0%, more preferably 45.0%, still more preferably 4%% and further preferably 35.0. %, further preferably less than 3 〇. 〇 C / ^, the upper limit of the content of the 〇 component may be preferably 25.0% 'more preferably 2%, more preferably 15.0/ . . In particular, in the second optical glass, the upper limit of the content of the component may be 10.0% or may be less than 6%. For example, MgC〇3, MgF2, CaC03, CaF2, Sr(N〇3)2, SrF2, BaC〇3, and Ba(N〇3)2 can be used as the CaO component, the SrO component, and the BaO component. The raw material is contained in the glass. In the optical glass of the present invention, the mass of the R〇 component (wherein the ruler is selected from one or more of the group consisting of Mg, Ca, Sr, and Ba) is preferably 55.0% or less. Thereby, the devitrification of the glass caused by the excessive scale component is lowered, and the refractive index of the glass is hard to be lowered. Therefore, the upper limit of the mass of the R 〇 component of the total mass of the glass in terms of the oxide conversion composition is not preferably 55.0%, more preferably 45% by weight, still more preferably 40.0%, and most preferably It is 35.0%. Further, the mass and the upper limit of the content of the ruler component may be preferably 25.0%, more preferably 20.0%, still more preferably 15.0%, and most preferably 1〇.〇°/0.

The Na20 component is a component which improves the meltability of glass and is an optional component in the optical glass of the present invention. In particular, when the content of the NhO component is 20.0% or less, the refractive index of the glass is hardly lowered, and the stability of the glass is improved to prevent devitrification or the like from occurring. Therefore, the upper limit of the content of the 〇^〇 component of the total mass of the glass which is different from the oxide s 157771'doc 37·201231427 is preferably 20.0%, more preferably 15%, more preferably 1 〇〇%, more preferably 8 〇%, and most preferably 5.0%. The Na 2 〇 component can be contained in the glass, for example, using Na 2 CO 3 , NaN03, NaF, NhSiF 6 or the like as a raw material.

The Rn2 〇 component (wherein Rn is selected from the group consisting of 以, Ν & κ) is a component which improves the meltability of the glass and lowers the glass transition point to lower the devitrification of the glass. Here, when the content of the Rn2 bismuth component is 25 〇% or less, the refractive index of the glass is hardly lowered, and the stability of the glass is improved to reduce the occurrence of devitrification or the like. Therefore, the mass and the upper limit of the Rr^O component with respect to the total mass of the glass in terms of the oxide conversion composition are preferably 25.0%, more preferably 20.0%, and most preferably 15% by weight. In particular, in the fourth optical glass, the upper limit of the mass and the mass may be set to 丨〇 〇 %, and the upper limit may be set to 5.0%.

The ZnO component is an element of the optical glass of the present invention which is a component which improves the meltability of glass, lowers the glass transition point, and easily forms a stable glass. In particular, the photoelastic constant of the optical glass is slightly suppressed by setting the content of the ZnO component to 30·0% or less. Therefore, the polarizing characteristics of the optical glass can be improved, and the color rendering property in the projector or the camera can be improved. Therefore, the upper limit of the content of the Ζη〇 component relative to the total mass of the glass of the oxide-converted composition is preferably 30.0%', more preferably 25%, more preferably 20.0%', and still more preferably 15.0%. Further, it is preferably 12% by weight, and further preferably the vehicle is preferably 10% and further preferably 8.7% and further preferably 7.7%. Yougan 15777l.doc •38- 201231427 is 'in the first optical glass, the upper limit of the content of the Zn0 component may be set to 5.0%. The Zn0 component can be contained in the glass, for example, by using Zn ruthenium or the like as a material.

The GeCh component is a component having an effect of increasing the refractive index of glass and improving the resistance to devitrification, and is an optional component in the optical glass of the present invention. However, since the raw material of the Ge 2 component is expensive, if the amount is large, the material cost rises. Therefore, the obtained glass is not practical. Therefore, the upper limit of the content of the total amount of the glass relative to the composition of the telluride composition is preferably 10·0Λ, more preferably 8.0%, still more preferably 5% by weight, and still more preferably 2.0%, preferably less than 2%. The Ge〇2 component can be contained in the glass, for example, as a raw material. The P2〇5 component has the effect of lowering the liquidus temperature of the glass and improving the resistance to devitrification. The component is an optional component in the optical glass of the present invention. In particular, the content of the P2〇5 component is 10% by mole or less, whereby the chemical durability of the glass, particularly the decrease in water content, can be suppressed. The upper limit of the content of the P2〇5 component relative to the total mass of the glass in the oxide-converted composition is preferably 10.0%, more preferably 8% by weight, still more preferably 5% by weight, most preferably P2〇5 component. For example, a1(p〇3)3, Ca(p〇A, Ba(P〇3)2, BP〇4, H3P〇4 or the like can be used as a raw material and contained in the glass.

The Ga2〇3 component is a component which is easy to form a stable glass and is an optional component in the optical glass of the present invention. In particular, the content of the Ga2〇3 component is set to 1 〇·〇% or less, whereby the decrease in the Abbe number of the glass can be suppressed. Therefore, the upper limit of the Ga203 component of the total mass of the glass in terms of the oxide conversion composition is preferably 1 〇 〇 %, more preferably 8.0%, and further preferably 8.0%.

S 157771.doc _ 201231427 is 5, the best is 2_〇%. For example, the component 3 can be contained in a glass using, for example, Ga(OH) 3 or the like as a raw material. The composition of the optical glass of the present invention is an arbitrary component of the optical glass of the present invention. However, (10) has the following problem of 'that' or the part of the glass that is in contact with the (four) glass. In the sleek melting tank (4), when the raw material is broken, it may be combined with 16. Therefore, the upper limit of the content ratio of the (four) component of the total mass of the glass in terms of the oxide-converted composition is preferably 1% ’%', more preferably 8%, and most preferably 5%. The Te〇2 component can be contained in the glass, for example, using Te〇2 or the like as a raw material.

The Sn 2 component is a component which lowers the oxidation of the molten glass to purify the molten glass and hardly deteriorates the transmittance of the glass to light, and is an optional component in the optical glass of the present invention. In particular, the content of the component is set to 5 〇% or less, whereby the coloring of the glass or the devitrification of the glass caused by the reduction of the molten glass is less likely to occur. Further, the alloying of the Sn 2 component and the dissolving device (especially a noble metal such as & etc.) is lowered, so that the life of the dissolving device can be extended. Therefore, the upper limit of the total mass of the glass of the oxide-converted composition is preferably 5.0%, more preferably 3.3%, still more preferably 1.0%, more preferably 〇.7%, preferably 〇5%. The Sn 〇2 component can be contained in the glass by using SnO, Sn 〇 2, SnF 2, S11F4 or the like as a raw material, for example, 0 st > 2 〇 3 component is used to defoam the molten glass. The component is a component of the optical glass of the present invention. In particular, when the content of the St 2 2 component is 1.0% or less, excessive foaming during melting of the glass is difficult to occur, and it can be 15777I. Doc -40- 201231427 It is difficult to alloy the Sb2〇3 component with a dissolving device (especially a noble metal such as Pt). Therefore, the upper limit of the content of the Sb2〇3 component relative to the total mass of the glass in the oxide conversion composition is set to be Preferably, it is J 〇%, and more preferably it is 0.5%. The Sb2 〇3 component can be contained in glass, for example, sb2〇3, 补2〇5, NaeebaOrSH2, etc. The component which purifies and defoams the glass is not limited to the above 讥2〇3 component, and can be used in the field of glass manufacturing. A known decontaminant 'defoaming agent or a combination thereof. <Components not to be included> Next, the components which should not be contained in the optical glass of the present invention and the components which are not included in the description are described. In the optical glass, other components may be added as needed within the range which does not impair the characteristics of the glass of the invention of the present invention. Among them, the Ge02 component causes the dispersibility of the glass to be improved, and therefore it is preferably not substantially contained. Further, in addition to Ti, Zr, Nb, w, La, Gd, γ, Yb, and Lu, each transition metal component such as V ' Cf ' Μ η 'Fe, Co, Ni, Cu, and M 系 is used for each When it is contained alone or in combination and in a small amount, it also has a property that the glass is colored and absorbs at a specific wavelength of the visible region. Therefore, it is preferable that the optical glass having a wavelength of the visible region is substantially not included. Further, lead compounds such as Pb〇 and arsenic compounds such as AS2〇3, and Th,

In recent years, various components of Cd, Dingbu 0s, Be, and Se have a tendency to be controlled as harmful chemicals, and not only the manufacturing steps of glass, but also measures for environmental countermeasures are required for the processing steps and the points after the production. Therefore, in the case of the weight of the 15777, d〇C -41- 201231427 'brother's shirt, it is better not to include it except for the inevitable mixing. Thereby, the optical glass does not substantially contain the substance of the filth. It is imperative that the optical glass can be manufactured, processed and discarded without implementing special environmental measures. The glass composition of the present invention is represented by the mass % of the total glass of the composition in terms of oxide, and therefore is not directly represented by the description of the mole %, but is in accordance with the requirements of the present invention. The enthalpy of each component present in the characteristic glass composition: a:. /Main, / τ甘你 < The composition of the ear knives of the knives is approximately the following values in terms of oxide composition. B2O3 composition 1〇.〇~75.0 mol% and

La2〇3 Ingredient 0~25.〇111〇1% and/or Bi2〇3 component〇~4.0mol% and/or Ti02 component 0~30.0 mol% and/or W03 component 0~10.0 mol% and/or Nb205 component 0~10.0 mol% and/or K20 component 0~15.0 mol% and/or Ta2〇5 component 〇~1〇.〇111〇1% and/or Zr〇2 composition 〇~25.〇111〇1% and / Or Li2〇 composition 〇~40.〇111〇1% and/or Gd2〇3 ingredient 〇~20.〇111〇1% and/or Y203 ingredient 〇~15.〇111〇1% and/or Yb2〇3 component 〇~l〇.〇m〇l% and/or Lu2〇3 ingredients 0~10.0m〇l% and/or 157771.doc -42- 201231427

MgO component 0~50.0mol% and/or CaO component 0~50.0mol°/〇 and/or SrO component 0~50.0 mol% and/or BaO component 0~55.0 mol% and/or SiO2 component 0~70.0 mol% and / or - ZnO composition 0~30.0 mol ° /. And / or

Ge〇2 Component 0~20.〇111〇1% and/or P2〇5 component〇~1〇.〇mol% and/or Al2〇3 component 0~40.0 mol% and/or Ga2〇3 composition〇8 〇111〇1% and/or Na20 component 0~25.0 mol% and/or Te02 component 0~8.〇111〇1% and/or Sn〇2 component 〇~5.〇111〇1°/() and / or Sn 〇 2 component 0 ~ l. Omol% and / or Sb2 〇 3 components 〇 ~ 〇 · 5 mol% and one or more of one or two or more of the above metal elements are replaced by one or all of the oxides Fluoride as a total amount of F 0 to 75.0 mol% In particular, the composition represented by the first optical glass molar % is based on the composition of the oxidation, preferably 1 ^ 203 component 5.0 to 25. 〇 111 〇 1% and

Ta2〇5 component 〇~5.0mol ° / 〇 and / or Li2 〇 composition 〇 ~ 25.0 mol% and / or £ 157771.doc -43 - 201231427

MgO component 0~35.0 mol% and/or CaO component 0~35.0 mol% and/or SrO component 0~25.0 mol% and/or BaO component 0~25.0 mol% and/or Si〇2 component 〇~60.〇mol % and / or AI2O3 composition 〇 ~ 20. 〇 1 « 〇 1% and / or Sn02 composition 0 ~ 1.0 mol%. Further, the composition expressed by the second optical glass molar % is preferably an oxide composition, preferably 1 ^ 2 〇 3 component 5.0 to 25. 〇 111 〇 1% and

Li2 is 0~30.0 mol% and/or

Lu2〇3 Ingredients 〇~5.〇111〇1% and/or

MgO composition 〇~35.0 mol% and/or

CaO composition 〇~35.0mol% and / or

SrO composition 0~25.0 mol% and/or

BaO composition 〇~25.0mol% and / or

Si〇2 composition 0~60.〇111〇1% and/or

Al2〇3 component 0~20.0 mol% and/or

Sn〇2 component 0~1.0 mol%.

In particular, the composition of the third optical glass Mohr%++ A is preferably a Gd2〇3 component 0~15.〇111〇1% and/or a Ta205 component〇~ 3.0 mol% and / or 157771.doc • 44- 201231427

ZnO component 0 to 25·〇mol% and/or 八12〇3 component 0~20.〇111〇1% and a part or all mol% ～75.0 and one or more oxides of each of the above metal elements The total amount of fluoride substituted by the portion is more than 〇 mol%. Further, the composition represented by the fourth optical glass Moer % is preferably an oxide conversion composition, preferably a B2O3 component of 10.0 to 75.0 mol%.

The composition of La203 is 10.0~25.0 mol% and the composition of 八12〇3 exceeds 〇111〇1%~40.〇111〇1. /() as well as

Ta2〇5 Ingredient 〇~4.0]11〇1% and/or Li2〇 component 〇~15.〇111〇1% and/or MgO component 0~35.0 mol°/. And/or CaO component 0~50.〇mol% and/or SrO component 0~35.0m〇l%&/4 BaO component 0~50.0 mol% and/or ZnO component 0~25.0 mol% and with the above metals The total amount of F of the fluoride which is partially or completely substituted by one or two or more kinds of oxides of the element exceeds 〇m〇1% to 75〇mol%. [Manufacturing Method] 157771.doc • 45 -

S 201231427 The optical glass of the present invention is produced, for example, as follows. In other words, the raw materials are uniformly mixed so that the respective components are within a specific content, and the produced mixture is poured into platinum crucible, quartz crucible or alumina crucible, and then coarsely melted, and then the crucible, platinum crucible, and Platinum alloy ruthenium or osmium, and melted in the temperature range of 900 to 1400 ° C for 1 to 5 hours, stirred to homogenize and defoamed, etc., and then lowered to 12 〇 (the temperature below rc, fine It is produced by processing and stirring to remove streaks and molding using a molding die. Here, as a method of obtaining a glass formed by using a molding die, a method of flowing molten glass to one end of a molding die while self-forming the other end of the mold A method of extracting the formed glass from the side or a method of forming a glass formed body by a single press, or a method of casting the molten glass by cooling as in a so-called suspension forming to form a glass into a (4) method. Physical properties;) The optical glass of this month preferably has a specific refractive index and dispersion (Abbe number). Here, the refractive index of the optical glass of the present invention (preferably i-5, more, and further preferably (d). In particular: = the lower limit of the refractive index (nd) of the H-th optical glass is preferably More preferably, the lower limit of U, more preferably 1.73, and further preferably (75, most preferably I?? and also the refractive index of the fourth optical glass (5)) is preferably 1.57, = 1.60, preferably The upper limit of the refractive index κ of the optical component of the present invention is not particularly limited, and is approximately 22 Å or less, more specifically 2·10 or less, and specifically 2 Å or less. Situation 157771.doc •46- 201231427 Most. In particular, the upper limit of the refractive index (6) of the third optical glass may be preferably 1.70, more preferably less than 17 Å, and most preferably 丨69. The lower limit of the Abbe number (5) of the optical glass of the present invention is preferably 39 Å or more preferably 40 Å and more preferably 41. In particular, the lower limit of the Abbe number (Vd) of the first and fourth optical glasses may be preferably 乜, more preferably 47, and most preferably 49. X, the lower limit of the Abbe number (6) of the third optical glass may be preferably 50, more preferably 52, and most preferably 53. On the other hand, the upper limit of the Abbe number (Vd) of the optical glass of the present invention is not particularly limited, and is approximately 63 or less, more specifically 61 or less, more specifically, the following, and more specifically 58 or less. More specifically, the situation below 57 is mostly. In particular, the upper limit of the Abbe number (vd) of the second optical glass of the present invention may be preferably 52, more preferably 51, and most preferably 5 Å. Here, the Abbe number (Vd) of the second optical glass of the present invention is between the refractive index (11(1) and preferably (~)2 (_125><11£1+265). The relationship 'better is to satisfy the relationship of (vd) 2 (-125xncj + 266), and it is preferable to satisfy the relationship of (Vd)g (_125x nd + 267). Further, the Abbe number of the optical glass of the present invention (Vd) Between the refractive index (nd) and preferably (Vd)g (_l〇〇xnd+22〇), more preferably (vd)g(-l〇〇Xnd+222) The relationship is optimal to satisfy the relationship of (Vd)g(_1〇〇Xnd+223). In particular, in the third optical glass, the Abbe number (...) is taken as the X-axis and the refractive index (nd) is Among the Xy orthogonal coordinates of the y-axis, it is preferable to have a range surrounded by four points of A (50, 1.70), B (60 ' uo), C (63, 1.60), and D (63, 1.70). The number and the refractive index. By these, the degree of freedom in optical design is widened, and even the thinning of the element 15777].doc •47-201231427 can achieve a larger amount of light refraction. The glass system has a higher partial dispersion ratio (0g, F). More specifically, the present invention The partial dispersion ratio (0g, F) of the optical glass is such that (eg, F) 2 (_〇〇〇17〇XVd+〇6375) or (0g,F)g (-2) is satisfied with the Abbe number (vd). 〇xl (T3xVd + 〇6498). The optical glass of the present invention can obtain an optical glass having a partial dispersion ratio (eg, F) which is more than a previously known glass containing a large amount of rare earth element components. The refractive index and low dispersion of the glass are now reduced, and the chromatic aberration of the optical element formed by the optical glass can also be reduced. Here, the lower limit of the partial dispersion ratio (Qg, F) of the first optical glass is preferably ( -0.00170>^+0.63750)' is better (_〇0〇17〇><, + 〇6395〇), and the best is (-0.0017〇xvd+0.641 50). On the other hand, for the first The upper limit of the partial dispersion ratio (eg 'f) of the optical glass is not particularly limited, and is, for example, (-0_00170><vd+0.65750), more preferably (_〇0017〇XVd+〇6555〇), and most preferably ( - 〇.〇〇17〇xvd+0.653750) is mostly the case. Also, the lower limit of the partial dispersion ratio (0g, F) of the optical glass is preferably (-2.0><10_3&gt ;^(1+0.6498)' is more preferably (_2(^1〇-3><~+ 〇6518), and most preferably (-2·0χ10 xvd+0.6558). On the other hand, the upper limit of the partial dispersion ratio (eg 'f) of the second optical glass is not particularly limited, and is, for example, (-2.0xl (T3xvd + 0, 6950), more preferably (_2〇xl〇-3xvd+) 〇693〇), the best is (-2.0><10-3>^+0.6910). In addition, the partial dispersion ratio of the second optical glass is defined by the line parallel to the regular line and Abbe In the case of the relationship of the number (vd), the 'partial dispersion ratio (eg, F) becomes, for example, (_17χ l〇-3XVd+0,63450) or more, more specifically (_l7xl〇-3xVd+〇6375〇) 157771.doc • 48-201231427 or more, more specifically (-1·7 xio·3 XVd+0.63950) or more, and more specifically (-1.7><10-3>^£1+0.64150) or more, for example, It is (-1.7xl〇-3xvd+〇.67750) below, more specifically (1) 7χ1〇·3χ^+ 0.67550), and more specifically (_i.7xi〇_3xVd+〇67350). Further, the lower limit of the partial dispersion ratio (0g, F) of the second optical glass is preferably (-0.00170xvd+0.6375), more preferably (_〇〇〇17〇XVd+〇6395), and most preferably (-0.00l70xvd) + 0.6415). On the other hand, the upper limit of the partial dispersion ratio (Θ g ' F) of the third optical rupture is not particularly limited, and is approximately (-0.00170×vd+0.6575), more specifically (_〇〇〇17〇XVd+ 〇6555), and then specific g(-〇.〇〇17〇xvd+〇.6535) is mostly the case. Further, the partial dispersion ratio of the fourth optical glass, the lower limit of F) is preferably (-0.00170xvd + 0.6375), more preferably (_〇.〇〇17〇XVd+〇6395), and most preferably (-0.0〇17) 〇xVd+0.6415). On the other hand, the upper limit of the partial dispersion ratio (0g, F) of the fourth optical = glass is not particularly limited, and is approximately (-0.00170xvd + 0.6800) or less, more specifically (_〇〇〇ΐ7〇χ) , + 0.6790) below, and then specifically (_〇.〇〇17〇XVd+〇678〇) below ^ is mostly the case. Further, the preferred range of the partial dispersion ratio in the present invention varies depending on the Abbe number of the optical glass, and therefore is represented by a straight line parallel to the regular line. The partial dispersion ratio (4) of the optical glass of the present invention, F) is based on the Japanese Optical Glass Industry Association specification IQGIS() 1-2G()3. Further, the glass used in the measurement was obtained by using a cold cooling rate of _25 t/hr and a treatment by a quench furnace. Further, the optical glass of the present invention preferably has a glass transition point (Tg) of 650 ° C or lower. Thereby, extrusion molding at a lower temperature can be performed, so that the oxidation of the mold used in the press molding can be reduced to achieve a longer life of the mold. Therefore, the upper limit of the glass transition point (Tg) of the optical glass of the present invention is preferably 650 ° C, more preferably 620 ° C, and most preferably 600 ° C. Further, the lower limit of the glass transition point (Tg) of the optical glass of the present invention is not particularly limited, and the glass transition point (Tg) of the glass obtained by the present invention is approximately 100 ° C or higher, specifically 150 ° C. The above, and more specifically 200 °c or more, are mostly the case. The glass transition point (Tg) of the optical glass of the present invention was calculated by measurement using a differential thermal measuring device (STA 409 CD manufactured by NETZSCH-Geratebau Co., Ltd.). Here, the sample particle size at the time of measurement was set to 425 to 600 μηι, and the temperature increase rate was set to 10 ° C/min. Further, the optical glass of the present invention preferably has less coloration. In the optical glass of the present invention, if the transmittance is 10 mm, the wavelength of the spectral transmittance of 7 〇 ° / ◦ (λ7 〇) is 500 nm or less, more preferably 480 nm. Below, the best is below 450 nm. In particular, in the optical glass of the present invention, the wavelength indicating the spectral transmittance of 80% (λ8 〇) in the sample having a thickness of 10 mm is preferably 500 nm or less, more preferably 480 nm or less, and most preferably 450 nm or less. . Further, in the optical glass of the present invention, the wavelength of 5% of the spectral transmittance (λ5) in the sample having a thickness of 10 mm is 450 nm or less, more preferably 430 nm or less, and most preferably 410 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 used as a material of an optical element such as a lens. 157771.doc -50- 201231427 The transmittance of the optical glass of the present invention is measured in accordance with the Kobe Optical Glass Industry Association specification JOGIS02. Specifically, for the opposite parallel grinding product with a thickness of 1〇±〇丨, the spectral transmittance of 2〇〇~8〇〇 is measured according to JISZ8722' hu80 (wavelength at 80% transmittance), λ7〇 (penetration) The rate is 7 〇% at I wavelength) and λ5 (wavelength at 5% transmittance). Further, the optical glass of the present invention preferably has a small photoelastic constant. In particular, in the optical glass of the present invention, the photoelastic constant (β) at a wavelength of 5463 nm is 2. 〇xl 〇 5 nm.cm-i.Pa_i or less, more preferably i 5 χ 1 〇 _5 咖 Pa· 1 or less, further preferably 1 〇 x l 〇 -5 or less is preferably 0.7 X 10 · 5 nm. cm - i. Pa - i or less. Thereby, the partial dispersion ratio of the optical glass is increased, and the polarization characteristics of the transmitted light are also improved, so that the optical glass is used to reduce the chromatic aberration when used in an optical system of a projector or a camera (especially including a polarizer). It also suppresses the disordered reflection of light inside the optical element. That is, the color rendering properties in such projectors or cameras can be further improved. The photoelastic constant (β) of the optical glass of the present invention is a sample of a circular plate having a diameter of 25 mm and a thickness of 8 mm which is oppositely ground, and a compressive load of F[Pa] is applied in a specific direction, and is measured at the center of the glass at this time. The optical path difference δ [ηιη] of the light having a wavelength of 546.1 nm is generated. Then, using the obtained values of ρ and δ and the thickness d [cm] of the glass ' and calculating the photoelastic constant β [1 (Τ5 nm.cn Ti.Pa-1) according to the relationship of 5 = pxd >< F Further, the measuring light source having a wavelength of 546.1 nm is an ultrahigh pressure mercury lamp. Further, the optical glass of the present invention preferably has a high resistance to devitrification. In particular, the optical glass of the present invention preferably has 1200. The lower liquidus temperature below. More specifically, the upper limit of the liquidus temperature of the optical glass of the present invention

S 157771.doc -51 - 201231427 , preferably 1 (10). c, the best is (1) generation. By the fact that the glass is improved and the crystallization is lowered, the devitrification resistance from the melt, .../glass formation can be improved, and the influence of the optical element using glass on the optical characteristics can be reduced. The other surface is not particularly limited to the lower limit of the liquidus temperature of the optical glass of the present invention, and the liquid phase temperature of the glass obtained by the present invention is approximately 500 ° C or more, specifically, more than or equal to, and further, Most cases are above 5 600 C. In addition, the "insulation test" in the present specification is performed by the following method. In order to confirm that the glass has high resistance to devitrification, the glass raw material is placed in a platinum crucible of 3 cc, and the lid is placed on the mmic. Dissolve 1 g to 2 g minutes in the furnace, mix and homogenize it, and then [suppress the obtained glass in the furnace set to ~η $ for 2 hours in the furnace, observe the surface and inside of the glass, and Crystallized from the contact surface with the inner wall of the crucible. [Preform and optical element] A glass molded body can be produced from the produced optical glass by, for example, molding by reheat extrusion molding or precision press molding. In other words, a preform for press molding can be produced from optical glass, and the preform can be subjected to reheat extrusion molding, followed by polishing to prepare a glass molded body, or, for example, a preform produced by polishing. The glass molded body was produced by precision extrusion molding. Further, the method of producing the glass formed body is not limited to these methods. The glass forming system thus produced is effectively utilized for various optical elements, and among them, it is particularly preferably used for optical elements such as lenses or prisms. By this, the color chromatic aberration caused by the chromatic aberration 157771.doc -52 - 201231427 in the transmitted light of the optical system provided with the optical element is lowered. Therefore, when the optical element is used in the case of a camera, the object to be imaged can be more accurately displayed, and when the optical element is used in a projector, the desired image can be projected with higher brightness. [Examples] Examples of the present invention (No. A1 to No. A13, No. B, No. B23, No. Cl to No. C6, No. D1 to No. D36) and comparative examples (No. al) Composition of No. cl, No. dl), and refractive index (nd) and Abbe number (vd), partial dispersion ratio (0g 'F), glass transition point (Tg), and transmittance of the glass. The wavelength at % (λ - the wavelength at which the transmittance is 5% (λ5) and the value of the liquidus temperature are shown in Tables 1 to 11. Further, the following examples are merely illustrative purposes, and are not limited thereto. Examples of the optical glass and comparative examples (No. 〜1 to No. Α13, No. Β1 to No. Β23, No. Cl~No. C6, No. D1 to No. D36) of the present invention. · The glass of al, No. cl, and No. dl) is a raw material for each component, which is equivalent to oxides, hydroxides, carbonates, acid salts, fluoride cerium oxides, meta- sulphate compounds, etc. Usually, the high-purity raw material used in the optical glass is weighed and uniformly mixed in such a manner as to achieve the ratio of the composition of each of the examples and the comparative examples shown in Tables 1 to 丨丨, and then put into the platinum crucible. According to the glass group After the melting is difficult, the electric furnace is dissolved in a temperature range of 1000 to 1400 ° C for 6 hours, stirred to homogenize, and defoamed, etc., and then the temperature is lowered to 1 2001 or less, and the mixture is homogenized. Cast into a mold and slowly cool to produce glass. Here, 'Examples (No. A1 to No. A13, No. B1 to No. B23, No. Cl to No. C6, No. D1 to No. D36) and Comparative example (No. al, N〇. cl, 157771.doc •53·201231427

The refractive index (nd) and the Abbe's number (Vd) and the partial dispersion ratio (Qg'F) of the glass of No. dl) are measured based on the specifications of the 光学本光光工工业会j〇Gis〇 1 __2〇〇3. Then, with respect to the calculated values of the Abbe number (Vd) and the partial dispersion ratio (0g 'F), the intercept of the relationship (0g 'F)=-axvd+b is calculated to be an intercept of 0.0017 and 0.0020. b. Further, the value of the calculated refractive index (nd) is a value of the relationship - l〇〇xnd + 220. Further, the glass used in the measurement was obtained by subjecting the cooling rate of the cold cooling to _25 〇 c / hr and treating it in a quench furnace. In addition, the glass transition point (Tg) of the glass of the examples (No. D1 to No. D36) and the comparative example (No. dl) was performed by using a differential heat measuring device (STA TZ CD manufactured by NETZSCH-Gemebau Co., Ltd.) Calculated by measurement. Here, the sample particle size at the time of measurement was set to 425 to 6 Torr, and the temperature increase rate was set to i 0 °c/min. Further, the transmittances of the glass of the examples (No. D1 to No. D36) and the comparative example (No. dl) were measured in accordance with the specifications of the Japan Optical Glass Industry Association. Further, in the present invention, the transmittance of the glass is measured, thereby calculating the presence or absence of coloration. Specifically, for a parallel-surface grinding product having a thickness of 1 〇士〇. 1 mm, a spectroscopic transmittance of 200 to 800 nm is measured according to JIS Z8722, and a wavelength of 08〇) and a heart (penetration at a transmittance of 8〇%) are calculated. The wavelength is 5%). Further, in the examples (No. D1 to No. D36) and the glass of the comparative example (Νο· dl), the phase temperature was measured by the following method, #, and the pulverized glass sample was placed at intervals of platinum at 'mm. On the board, take it out in the oven with 800 °C to 120 (the X tilt of the TC is taken for 3 minutes, and after cooling, observe the crystal in the glass sample with a microscope with a magnification of 8〇J 57771 .doc -54· 201231427 times. At this time, as a sample, the optical glass was pulverized into a pellet having a diameter of about 2 mm. [Table 1] ____ Example A1 A2 A3 A4 A5 A6 A7 A8 b2〇3 22.63 22.63 22.63 22.63 23.11 18.95 18.95 18.53 La2〇 3 37.43 37.43 44.44 37.43 43.28 47.00 47.00 45.98 Bi203 0.00 0.00 0.00 0.00 0.22 0.00 0.00 0.00 Ti〇2 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.2 0.2 0.2 0.2 0.2 0.2 0.2 0.2 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2. 2.18 K,0 〇.〇〇0.00 0.00 0.00 0.00 0.00 0.00 0.00 Zr02 2.69 2.69 2.69 2.69 2.75 2.79 2.79 2.73 Ta2〇5 0.00 0.00 0.00 0.00 0.00 0.00 2.23 0.22 LhO Gd203 30.72 23.71 23.71 23.71 24.21 24.52 2 4.52 23.99 Y2O3 Yb203 0.00 7.01 0.00 0.00 0.00 0.00 0.00 0.00 Lu2〇3 MrO 〇.〇〇0.00 0.00 7.33 0.00 0.00 0.00 0.00 CaO 〇.〇〇0.00 0.11 0.00 0.00 0.00 0.00 0.00 SrO 0.00 0.22 0.00 0.00 0.00 0.00 0.00 0.00 BaO 0.32 0.00 0.00 0.00 0.00 0.00 0.00 0.00 SiCh 3.23 3.23 3.23 3.23 3.30 3.34 3.34 3.27 ZnO 0.75 0.86 0.97 0.75 0.88 0.89 0.89 0.87 Ge〇2 P7O5 ai2〇3 Na2〇〇.〇〇0.00 0.00 0.00 0.00 0.00 0.22 0.00 Sn〇2 Sb2〇 3 0.05 0.05 0.05 0.05 0.06 0.06 0.06 0.05 Total 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 F (addition ratio) 7.84 7.84 7.84 7.84 10.08 11.51 11.51 11.26 F+Bi+Ti+W+Nb+K 10.00 10.00 10.00 10.00 12.50 13.96 11.51 15.62 (F+Bi+Ti+W+Nb+K)/(Zr+Ta+Li) 3.71 3.71 3.71 3.71 4.55 5.01 2.30 5.31 La+Gd+Y+Yb+Lu 68.15 68.15 68.15 61.14 67.49 71.52 71.52 69.96 Mg+Ca+ Sr+Ba 0.32 0.22 0.11 7.33 0.00 0.00 0.00 0.00 nd 1.77414 1.77168 1.77072 1.73661 1.76743 1.77589 1.76898 1.77082 Vd 50.6 49.2 49. 3 56.6 49.5 50.2 52.2 51.5 157771.doc •55· s 201231427 [Table 2] Example A9 A10 All A12 A13 B2〇3 18.95 16.72 19.07 18.95 18.95 La2〇3 47.00 47.00 48.90 47.00 47.00 Bi203 0.00 0.00 0.00 0.00 0.00 Ti02 0.33 〇 .〇〇〇.〇〇〇.〇〇〇.〇〇W〇3 0.00 0.00 0.00 0.00 0.00 Nb205 2.23 2.23 0.00 0.00 0.00 k2o 0.00 0.00 0.45 0.00 0.00 Zr02 2.79 2.79 2.80 3.01 2.79 Ta2〇5 0,00 0.22 0.00 0.00 0.00 Li20 Gd2〇3 24.52 24.52 24*68 24.52 26.97 y2〇3 Yb203 0.00 0.00 0.00 0.00 0.00 LU2O3 MgO 0.00 0.00 0.00 0.00 0.00 CaO 0.00 0.00 0.00 0.00 0.00 SrO 0.00 0.00 0.00 0.00 0.00 BaO 0.00 2.23 0.00 2.23 0.00 S1O2 3.34 3.34 3.37 3.34 3.34 ZnO 0.78 0.89 0.67 0.89 0.89 Ge〇2 P2〇5 Al203 Na2〇0.00 0.00 0.00 0.00 0.00 Sn02 Sb203 0.06 0.06 0.06 0.06 0.06 Total 100.00 100.00 100.00 100.00 100.00 F (addition ratio) 11.51 11.51 12.24 11.51 11.51 F+Bi+Ti +W+Nb+K 14.07 13.74 12.69 11.51 11.51 (F+Bi+Ti+W+Nb+K)/ (Zr+Ta+Li) 5.05 4.57 4. 52 3.83 4.13 La+Gd+Y+Yb+Lu 71.52 71.52 73.58 71.52 73.98 Mg+Ca+Sr+Ba 0*00 2.23 〇.〇〇2.23 〇.〇〇nd 1.76346 1.76924 1.76334 1.7574 1.76374 vd 53.7 51.1 53.2 51,6 53.4 -56- 157771.doc 201231427 [Table 3] Example B1 B2 B3 B4 B5 B6 B7 B8 02〇3 16.46 17.91 20.03 18.99 21.91 15.65 15.65 15.65 La2〇3 52.44 32.81 43.88 41.76 39.43 39.43 39.43 39.43 ΒΪ2〇3 0.00 0.00 0.00 0.00 0,00 0.00 〇.〇〇0.00 Nb205 4.17 〇.〇〇2.23 2.22 2.09 5.22 5.22 5.22 Ti02 4.51 5.17 2.41 2.40 4.17 0.00 0.00 3.13 W03 0.00 0.00 0.00 1.92 0·00 0.00 0.00 0.00 K20 0.00 〇.〇〇0.00 0.00 0.00 0.00 0.00 0.00 Ta2〇5 0.00 0.00 0.00 1.77 〇.〇〇0.00 0.00 〇.〇〇Gd2〇3 2.71 29.47 8.53 15.11 22.96 22.96 26.09 22.96 y2〇3 9.65 4.36 5.16 5.72 0.00 0.00 0.00 0.00 Yb2〇3 0.00 0.00 7.23 0.00 0.00 0.00 0.00 0.00 Zr02 5.95 6.25 4.65 6.07 2.61 2.61 2.61 2.61 Li20 0.00 0.21 0.48 0.10 0.00 0.00 0.00 0.00 Si02 2.35 2.76 3.99 2.53 3.13 3.13 3.13 3.13 MgO 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 CaO 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 SrO 0.90 0.00 0.48 0.48 0.00 0.00 0.00 0.00 BaO 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 A 1203 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Sb203 0.05 0.05 0.04 0.05 0.05 0.05 0.05 TOTAL 100.00 100.00 100.00 100.00 100.00 100.00 100.00 100.00 F 6.56 6.02 6.31 5.59 7.59 7.59 7.59 7.59 (F+Bi+Ti+W+Nb+K) 15.24 11.20 10.95 12.12 13.85 12.81 12.81 15.94 (Bi+Ti+W+Nb+Ta) 8.68 5.17 4.64 8.31 6.26 5,22 5.22 8.35 La+Gd+Y+Yb+Lu 70.76 72.89 69.44 68.65 64.99 64.99 68.12 64.99 (La+Gd+Y+Yb +Lu)/ (Bi+Ti+W+Nb+Ta) 8.15 14.09 14.98 8.26 10.38 12.46 13.06 7.79 (F+Bi+Ti+W+Nb+K)/ (Ta+Zr+Li) 2.56 1.73 2.13 1.53 5, 31 4.91 4.91 6.11 Mg+Ca+Sr+Ba 0,90 0.00 0.48 0.48 0.00 〇.〇〇〇.〇〇〇.〇〇nd 1.83058 1.84202 1.79024 1.82153 1.80296 1.79632 1.79961 1.82139 vd 42.0 40.7 45.6 43.3 43.5 46.1 46.1 44.5 9g ' F 0.57049 0.57226 0.59400 0.57007 0.5 8342 0.56109 0.56376 0.58613 -125xnd+265 36.2 34.7 41.2 37.3 39.6 40.5 40.0 37.3 Intercept b(a=0.0017) 0.64189 0.64145 0.67152 0.64368 0.65737 0.63946 0.64213 0.66178 Intercept b(a=0_0020) 0.65449 0.65366 0.68520 0.65667 0.67042 0.65329 0.65596 0.67513 •57 - 157771.doc 201231427 [Table 4] Example B9 B10 B11 B12 B13 B14 B15 B16 02〇3 15.65 17.84 23.91 17.78 17.84 18.04 18.07 18.07 La2〇3 39.43 35.30 37.56 33.44 35.30 48.48 49.45 47.33 Bi203 3.13 0.00 〇.〇〇 0.00 0.00 0.00 0.00 0.00 Nb205 5.22 2.10 2.08 2.09 0.00 1.06 1.06 2.13 Ti02 0.00 〇.〇〇2.08 〇.〇〇0.00 〇.〇〇0.00 0.00 W〇3 0.00 4.20 0.00 4.18 4.20 2.12 2.13 2.13 k2o 0.00 0.00 0.00 0.00 0.00 〇.〇 〇0.00 0.00 Ta2〇5 0.00 0.00 0.00 0.00 0.00 〇.〇〇0.00 0.00 Gd2〇3 22.96 23.09 22.87 23.01 23.09 23.34 23.39 23.39 y2〇3 0.00 0.00 〇.〇〇2.09 2.10 〇.〇〇0.00 〇.〇〇Yb2〇 3 0.00 0.00 〇.〇〇〇.〇〇〇.〇〇〇.〇〇0.00 〇.〇〇Zr02 2.61 2.62 2.60 2.61 2.62 2.65 1.59 2.66 Li20 0.00 0.00 0.00 〇.〇〇0.00 0.00 0.00 0.00 Si02 3.13 3.15 3,12 3.14 3.15 3.18 3.19 3.19 MgO 0.00 〇.〇〇〇.〇〇〇.〇〇〇.〇〇〇.〇〇0.00 0.00 CaO 0.00 3.77 〇.〇〇3.76 3.77 〇.〇〇0.00 0.00 SrO 0.00 0.00 0.00 0.00 0.00 〇.〇〇0.00 0.00 BaO 0.00 0.00 0.00 0.00 0.00 〇.〇〇0.00 0.00 ai2〇3 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 ZnO 7.83 7.87 5.72 7.84 7.87 1.06 1.06 1.06 Te02 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00bb〇3 0.05 0.05 0.05 0.05 0.05 0.05 0.05 TOTAL 100.00 100,00 100.00 100.00 100.00 100.00 100.00 100.00 F 7.59 8.66 6.96 8.02 8.66 10.65 10.98 10.98 (F+ Bi+Ti+W+Nb+K) 15.94 14.96 11.12 14.30 12.86 13.84 14.17 15.23 (Bi+Ti+W+Nb+Ta) 8.35 6.30 4.16 6.28 4.20 3.18 3.19 4.25 La+Gd+Y+Yb+Lu 64.99 61·02 63.04 61.15 63.11 74.48 74.43 73.37 (La 十 Gd+Y+Yb+Lu)/ (Bi+Ti+W+Nb+Ta) 7.79 9.69 15.16 9.74 15.03 23.40 23.34 17.26 (F+Bi+Ti+W+Nb+K) / (Ta+Zr+Li) 6.11 5.70 4.28 5.47 4.90 5.22 8.89 5.73 Mg+Ca+Sr+Ba 0.00 3.77 0. 00 3.76 3.77 0.00 0.00 0.00 nd 1.8066 1.7606 1.79344 1.75874 1.76998 1.77705 1.77429 1.78692 vd 45.2 48.6 46.6 49.2 47.4 50.1 50.3 47.7 0g, F 0.58019 0.58789 0.56448 0.55843 0.56028 0.55649 -125><nd+265 39.2 44.9 40.8 45.2 43.8 42.9 43.2 41.6 Wear Distance b (a=0.0017) 0.66281 0.66711 0.64812 0.63901 0.64545 0.64200 Wearing distance b (a=0.0020) 0.67739 0.68109 0.66288 0.65323 0.66048 0.65709 • 58 · 157771.doc 201231427 [Table 5] Example B17 B18 B19 B20 B21 B22 B23 Β2〇3 18.07 18.07 22.04 20.83 22.04 22.04 22.04 La2〇3 47.33 47.33 41.60 37.47 41.60 41.60 41.60 Bi2〇3 2.13 0.00 0.00 0.00 0.00 0.00 0.00 Nb205 0.00 0.00 2*10 1·98 2.10 2.10 2.10 Ti02 0.00 0.00 0.00 0.00 0.00 1.05 0.00 W〇3 2.13 2.13 0.00 4.96 0.00 0.00 1.05 K20 0.00 0.00 0.00 0.00 0.00 0.00 Τ^2〇5 0.00 2.13 1.05 0.00 1.05 0.00 0.00 Gd203 23.39 23.39 23.09 21.82 23,09 23.09 23.09 Y2〇3 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Yb203 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Zr02 2.66 2.66 2.62 2.48 2.62 2.62 2 .62 Li20 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Si〇2 3.19 3.19 3.15 2.98 3.15 3.15 3.15 MgO 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 3. 0.00 0.00 AI2O3 0.00 0.00 0.00 0,00 0.00 0.00 0.00 ZnO 1.06 1.06 0.52 7.44 0.52 0.52 0.52 Te02 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 8.66 8.66 (F+Bi+Ti+W+Nb+K) 15.23 13.11 10.76 14.16 10.76 11:81 11.81 (Bi+Ti+W+Nb+Ta) 4.25 4.25 3.15 6.94 3.15 3.15 3.15 La+Gd+Y+Yb+ Lu 73.37 73.37 67.31 61.77 67.31 67.31 67.31 (La+Gd 十Y+Yb+Lu)/ (Bi+Ti+W+Nb+Ta) 17.26 17.26 21.38 8.90 21.38 21.38 21.38 (F+Bi+Ti+W+Nb+K ) / (Ta+Zr+Li) 5.73 2.74 2.93 5.71 2.93 4.50 4.50 Mg+Ca+Sr+Ba 0.00 0.00 3.77 0.00 3.77 3.77 3.77 nd 1.77972 1.77926 1.75725 1.78543 1.75725 1.76099 1.75588 vd 48.3 49.2 51.3 46.4 51.3 49.9 51.0 eg ' f 0.55142 0.56233 0.55 766 0.56233 0,56562 0.56005 -125xnd+265 42.5 42.6 45.3 41.8 45.3 44.9 45.5 Intercept b (a=0.0017) 0.63506 0.64954 0.63654 0.64954 0,65045 0.64675 Intercept b (a=0.0020) 0.64982 0.66493 0.65046 0.66493 0.66542 0.66205 ·59· 157771.doc 201231427 [Table 6] Example Comparative Example Cl C2 C3 C4 C5 C6 cl b2o3 41.981 40.501 36.889 10.013 10.130 10.079 20.200 L^2〇3 33.714 41.152 32.813 16.265 16.455 16.373 15.795 Si02 6.972 6.726 10.522 25.841 26.143 26.012 18.485 Gd2〇3 0.000 0.000 0.000 0.000 0.000 0.000 0.000 Y2〇3 0.000 0.000 0.000 0.000 0.000 0.000 0.000 Yb203 0.000 0.000 0.000 0.000 0.000 0.000 0.000 Bi203 0.000 0.000 0.000 0.000 0.000 0.000 0.000 Ti02 0.000 0.000 0.000 0.640 0.648 0.645 0,000 Nb205 0.000 0.000 0.000 0.000 0.000 0.000 0.000 W 〇3 0.000 0.000 0.000 0.000 0.000 0.000 0.000 k2o 0.000 0.000 0.000 0.000 0.000 0.000 0.000 Ta2〇5 0.000 0.000 0.000 0.000 0.000 0.000 0.000 Zr02 2.724 2.628 4.162 6.099 6.171 6.140 3.400 Li20 0.316 0.305 0.000 0.000 0.000 0.000 0.000 MrO 0.000 0.000 0.000 0.000 0.000 0.000 0.000 CaO 6.101 2.110 3.748 1.454 1.471 1.463 0.000 SrO 0.000 0.000 0.000 10.166 10.284 21.206 0.000 BaO 4.358 2.879 6.723 26.898 15.519 15.442 41.601 Na20 0.000 0.000 0Ό00 0.000 0.000 0.000 0.000 ZnO 3.813 3.679 5.122 2.196 12.746 2.210 0.000 Al2〇3 0.000 0.000 0.000 0.325 0.329 0.327 0.500 Sb203 0.022 0.021 0.021 0.102 0.103 0.102 0.020 TOTAL 100.00 100.00 100.00 100.00 100.00 100.00 100.00 F 6.340 3.779 5.094 2.864 4.914 4.024 0.000 La+Gd+Y+Yb+Lu 33.714 41.152 32.813 16.265 16.455 16.373 - Gd+Yb 0.000 0.000 0.000 0.000 0.000 0.000 0.000 F+B i+Ti+W+Nb+K 6.340 3.779 5.094 3.505 5.562 4.668 0.000 Bi+Ti+W+Nb 0.000 0.000 0.000 0.640 0.648 0.645 0.000 F/(F+Bi+Ti+W +Nb+K) 1.000 1.000 1.000 0.817 0.884 0.862 - (Ta+Zr 屮Li)/ (F+Bi+Ti+W+Nb+K) 0.479 0.776 0.817 1.740 1.109 1.315 - Mg+Ca+Sr+Ba 10.458 4.988 10.471 38.517 27.274 38.111 41.601 Li+Na+K 0.316 0.305 0.000 0.000 0.000 0.000 0.000 nd 1.67603 1.68429 1.68787 1.67 1.65914 1.65867 1.671 vd 55.8 56.6 55.3 54.1 54.8 55.0 55.5 -100nd+220 52.397 51.571 51.213 53.000 54.086 54.133 52.9 0g 1 F 0.55 0.551 0.552 0.559 0.560 0.558 0.546 戠 distance b (a=0.00170) 0.64486 0.64722 0.64601 0.65097 0.65316 0.6515 0.64035 -60- 157771. Doc 201231427 [Table 7] Example D1 D2 D3 D4 D5 D6 D7 D8 B203 21.78 20.96 22.00 21.78 22.24 20.33 21.55 21.55 La2〇3 39.19 39.60 37.50 41.26 40.02 38.30 36.73 36.73 Al2〇3 7.36 7.44 7.44 7.36 7.51 7.59 7.28 7.28 Si02 3.11 3.14 3.14 3.11 3.18 3.21 3.08 3.08 W03 1.04 1.05 1.05 1.04 1.06 1.07 1.03 3.08 Zr02 2.59 2.62 2.62 2.59 2.65 2.68 2.57 2.57 Ta2〇5 〇.〇〇0.00 0.00 0.00 〇.〇〇0.00 0.00 0.00 Bi2〇3 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Ti02 0.00 0.00 1.05 0.00 0.00 1.07 3.08 1.03 Nb2〇5 2.07 2.10 2.10 0.00 0.00 2.14 2.05 2.05 MgO 0.00 0.00 0.00 0.00 0.00 〇.〇〇0.00 〇.〇〇CaO 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 SrO 〇.〇 〇0.00 0.00 0.00 0.00 0.00 0.00 0.00 BaO 〇.〇〇0.00 0.00 0.00 0.00 0.00 0.00. 00 Gd203 22.81 23.05 23.05 22.81 23.30 23.55 22.58 22.58 22.2 Y2O3 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Li20 〇.〇〇0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 π 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 100.0 100.0 100.0 100.0 F 8.23 832 8.32 8.23 8.41 8.50 8.15 8.15 F/Al 1.12 1.12 1.12 U2 1,12 1.12 1.12 1.12 Si+B 24.89 24.10 25.15 24.89 25.41 23.55 24.63 24.63 Ln/(Si+B) 2.49 2.60 2.41 2.57 2.49 2.63 2.41 2.41 La/B 1.80 1,89 1.70 1.89 1.80 L88 1.70 1.70 W+La+Zr+Ta 42.82 43.26 41.17 44.89 43.72 42.05 40.32 42.38 Bi+Ti+Nb+W 3.11 3.14 4.19 1.04 1.06 4.28 6.16 6.16 Mg+Ca+Sr +Ba 〇.〇〇0.00 0.00 0.00 0.00 0.00 0.00 0.00 Li+Na+K 0.00 0.00 0.00 0.00 0.00 0.00 0.000*00 0.00 La+Gd+Y+Yb+Lu 62.00 62.65 60.55 64.07 63.31 61.85 59.31 59.31 nd 1.73673 1.73924 1.74506 1.72992 1.72769 1.74824 1.75890 1.74905 vd 51.70 52.20 50.00 54.30 51.90 48.30 45.90 48.80 -100nd+220 46.33 46.08 45.49 47.01 47.23 45.18 44.11 45.10 eg ' f 0.556 0.554 0.557 0.5535 0.556 0.560 0.568 0.564 Cut length b (a= 0.0017) 0.644 0.643 0.642 0.646 0.644 0.642 0.646 0.647 Tg[°C] 596 598 595 599 580 603 605 599 λ80[ηιπ] 387 389 395 383 384 394 403 396 λ5[ηΐΐΐ] 324 324 334 322 322 334 343 337 Liquidus temperature [°c] 1030 1040 1040 1030 1030 1050 1060 1040 15777].doc -61 -

S 201231427 [Table 8] Example D9 D10 Dll D12 D13 D14 B2〇3 21.78 21.78 21.78 19.91 19.70 18.86 L^2〇3 41.26 41.26 43.85 37.50 41.26 37.50 ai2〇3 7.36 7.36 7.36 7.44 7.36 7.43 Si02 3.11 3.11 3.11 3.14 3.11 3.14 W03 1.04 1.04 1.04 1.05 1.04 1.05 Zr02 0.00 0.00 〇.〇〇2.62 0.00 2.62 Ta2〇5 0.00 0.00 〇.〇〇0.00 0.00 〇.〇〇Bi203 0.00 0.00 0.00 〇.〇〇〇.〇〇〇.〇〇Ti02 0 *00 0.00 0.00 1.05 0.00 1.05 Nb205 0.00 0.00 0.00 2.10 0.00 2.10 MrO 0.00 0.00 0.00 〇.〇〇0.00 〇.〇〇CaO 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 3 22.81 25.41 22.81 25.15 24.89 26.20 y2〇3 2.59 0.00 0.00 0.00 2.59 0.00 Li2〇0.00 0.00 0.00 0.00 0.00 0.00 Na20 0.00 0.00 0.00 0.00 0.00 0.002 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Sn〇2 0.00 0.00 0.00 0.00 0.00 0.00 Sb203 0.05 0.05 0.05 0.05 0.05 Total 100.0 100.0 100.0 100.0 100. 0 100.0 F 8.23 8.23 8.23 8.32 8.23 8.32 F/Al 1.12 1.12 1.12 1,12 1.12 1.12 Si+B 24.89 24.89 24.89 23.05 22.81 22.00 Ln/(Si+B) 2.68 2.68 2.68 2.72 3.01 2.89 La/B 1·89 1.89 2.01 1.88 2.09 1.99 W+La Ten Zr Ten Ta 42.30 42.30 44.89 41.17 42.30 41.17 Bi+Ti+Nb+W 1.04 1.04 1.04 4.19 1.04 4.19 Mg+Ca+Sr+Ba 0.00 〇.〇〇〇.〇〇〇.〇〇0.00 0.00 Li+Na+K 0.00 0.00 〇.〇〇0.00 0.00 0·00 La+Gd+Y+Yb+Lu 66.67 66.67 66.67 62.65 68.74 63.70 nd 1.72183 1.72324 1.72553 1.74855 1.73418 L75532 vd 56.00 55.00 54.80 49.00 53.80 49.30 -100nd+220 47.82 47.68 47.45 45.15 46.58 44.47 eg,f 0.553 0.553 0.554 0.564 0.555 0.564 Carrying distance b(a=0_0017) 0.648 0.647 0.647 0.647 0.646 0.648 Tg[°C] 618 602 599 595 590 598 λ80[ηπι] 381 382 382 393 384 396 λ5Γηπι] 320 321 321 334 322 333 Liquidus temperature [°c] 1040 1040 1050 1030 1060 1050 -62- 157771.doc 201231427 [Table 9] Example D15 D16 D17 D18 D19 D20 D21 D22 ΒΛ 23.91 23.91 23.57 23.24 23.13 23.24 22.77 24.20 La2〇3 32.79 32.79 27.68 39.67 42.91 42.65 43.14 38.93 ΑΙ2Ο3 8.51 1.11 0.66 2.17 2.51 2.52 3.13 3.97 Si02 3.42 3.42 3.37 3.32 3.30 3.32 3.25 3.46 W03 0.00 0.00 0.00 1.11 L10 1.11 1.08 0.00 Zr02 2.85 2.85 0.00 2.77 0.00 0.00 0.00 0.00 Ta2〇5 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Bi2〇3 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 2.01 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Sb203 0.06 0.06 0,06 0.06 0.06 0.06 0.05 0.06 Total 100.0 100.0 100.0 100.0 100.0 100.0 100.0 100.0 F 10.49 10.49 9.34 8.82 9.85 10.45 7.53 13.84 F/Al 1.23 9.46 14.24 4.07 3.92 4.14 2.40 3.48 Si+B 27.33 27.33 26.94 26.56 26.44 26.56 26.02 27.65 Ln/ (Si+B) 2.12 2.12 1.94 2.41 2.64 2.63 2.68 2.47 La/B 1.37 1.37 1.17 1.71 1.86 1.84 1.89 1.61 W+La+Zr+Ta 35.63 35.63 27,68 43.54 44.01 43.76 44,23 38.93 Bi+Ti+Nb+W 2.28 2.28 5.05 3.32 1.10 1.11 1.08 0.00 M^+Ca+Sr+Ba 0.00 0.00 6.50 0.00 0.00 0.00 〇.〇〇0.00 Li+Na+K 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0'00 La+Gd+Y+Yb+ Lu 57.84 57.84 52.38 64.02 69.90 69.76 69.71 68.32 nd 1.72196 1.75574 1.75045 1.74232 1.70453 1.70280 1.71917 1.69503 vd 52.30 49.30 45.80 51.30 60.50 57.00 55.60 57.50 -100nd+220 47.80 44.43 44.96 45.77 49.55 49.72 48.08 50.50 0g,F 0.556 0.56 0.566 0.558 0.55 0.552 0.554 0.552 Intercept b(a=0.0017) 0.645 0.644 0.644 0.645 0.653 0.649 0.649 0.650 Tg[°C] 580 578 581 610 581 580 615 560 λ8〇Γηιπ] 386 387 376 369 382 380 3 81 382 X5[nm] 316 315 310 302 318 318 319 315 Liquidus temperature [°c] 1020 1030 1020 1040 1030 1020 1040 1010 157771.doc -63-

S 201231427 [Table 10] Example D23 D24 D25 D26 D27 D28 D29 D30 B2〇3 24.06 26.90 20.97 23.17 22.87 22.92 22.87 22.97 L&2〇3 38.71 37.88 39.49 39.49 40.91 43.43 43.34 43.52 Al2〇3 3.28 3.21 2.52 2.52 1.85 2.49 2.69 2.28 Si〇2 3.44 3.36 3.31 1.10 3.27 3.27 3.27 3.28 W〇3 0.00 0.00 1.10 uo 1.09 1.09 1.09 1.09 Zr02 0.00 0.00 2.76 2.76 2.72 0.00 0.00 〇.〇〇Ta2〇5 0.00 0.00 2.21 2.21 0.00 〇.〇〇0.00 〇. 〇〇Bi203 0.00 0.00 0.00 0.00 0.00 〇.〇〇0.00 〇.〇〇Ti02 0.00 0.00 1.10 1.10 1.09 〇.〇〇0.00 0.00 Nb205 0.00 0.00 2.21 2.21 2.18 0.00 0.00 0.00 MgO 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 24. 〇0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Na20 0.00 0.00 0.00 0.00 〇.〇〇0.00 〇.〇〇0.00 k2o 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 100.0 100.0 100.0 100.0 100.0 100.0 100.0 100.0 F 13.16 11.19 8.76 8.76 7.38 8.67 9.39 7_94 F/Al 4.01 3.48 3.48 3.48 4.00 3.48 3.48 3.48 Si+B 27.50 30.27 24.28 24.28 26.14 26.20 26.14 26.25 Ln/(Si+B) 2.47 2.20 2.63 2.63 2.48 2.68 2.68 2.68 La/B 1.61 1.41 1.88 1.70 1.79 1.89 1.89 1.89 W+La+Zr+Ta 38.71 37.88 45.56 45.56 44.72 44.52 44.43 44.62 Bi+Ti+Nb+W 0.00 0.00 4.41 4.41 4.36 1.09 1.09 1.09 Mg+Ca+Sr +Ba 1.23 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Li Ten Na+K 0.00 0.00 0.00 〇.〇〇0.00 0.00 0.00 0.00 La+Gd+Y+Yb+Lu 67.93 66.47 63.77 63.77 64.88 70.Π 70.02 70.32 nd 1.69620 1.70133 1.75235 1.76810 1.75661 1.72252 1.71941 1.73308 vd 56.60 55.90 50.10 47.60 48.10 54.40 56.00 54.70 •100nd+220 50.38 49.87 44.77 43.19 44.34 47.75 48.06 46.69 0g,F 0.551 0.552 0.56 0.564 0.563 0.554 0.552 0.553 Cutting distance b (a=0.0017) 0.647 0.647 0.645 0.645 0.645 0.646 0.647 0.646 Tg[°C] 565 572 581 584 593 581 578 583 λ80[ηι*η] 380 381 395 399 392 385 383 384 X5[nm] 313 313 334 335 334 322 321 322 Liquidus temperature [°c] 1000 1020 1040 1050 1040 1020 1020 1040 -64- 157771.doc 201231427 [Table 11] Example Comparative Example D31 D32 D34 D34 D35 D36 dl B203 20.74 18.56 16.37 19.62 25.43 13.08 19.57 L^2〇3 45.61 47.80 49.98 32.82 36.89 32.80 26.08 ai2〇3 2.49 2.49 2.49 2.37 2.12 2.13 0.00 Si02 3.27 3.27 3.27 8.28 3.07 6.99 2.17 W03 1.09 1.09 1.09 0.00 0.00 0.00 0.00 Zr02 0.00 0.00 0.00 7.78 7.12 6.55 0.00 Ta2〇5 0.00 0.00 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0.00 0.00 0.00 0.00 0.00 0.00 SrO 0.00 0.00 0.00 0.00 0.00 0.00 0.00 BaO 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Gd203 24.01 24.01 2 4.01 22.19 8.88 16.82 30.44 Y2O3 2.73 2.73 2.73 0.00 3.26 0,00 0.00 Li20 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Na20 0.00 0.00 0.00 0.00 0.00 0.00 0.00 K20 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 5 0.00 0.00 0.00 1.10 0.00 0.00 0.00 Sn 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 0.00 3.48 - Si+B 24.01 21.83 19.65 27.89 28.49 20.07 21.74 Ln/(Si+B) 3.01 3.41 3.91 1.97 1.72 2.47 2.60 La/B 2.20 2.58 3.05 1.67 1.45 2.51 1.33 W+La+Zr+Ta 46.70 48.89 51.07 46,39 50.37 59.78 26.08 Bi+Ti+Nb+W 1.09 1.09 1.09 0.00 6.82 1.09 0.00 Mg+Ca+Sr+Ba 0.00 0.00 0.00 0.00 0.00 0.00 0.00 Li+Na+K 0.00 0.00 0.00 0.00 0.00 0.00 0.00 La+Gd+Y+Yb+ Lu 72.35 74.54 76.72 55.00 49.03 49.62 56.52 nd 1.73226 1.73883 1.74378 1.73972 1.77979 1.80125 1.76253 vd 54.60 54.90 50.70 51.50 46.00 46.60 49.9 -100nd+220 46.77 46.12 45.62 46.03 42.02 39.88 43.75 0g,F 0.552 0.553 0.559 0.59 0.57 0.56 0.558 Intercept b(a=0.0017) 0.645 0.646 0.645 0.678 0.644 0.643 0.643 Tg[°C] 581 580 578 605 580 620 407 λ80[ηιη1 384 384 386 388 408 406 347 λ5[ηιη] 322 323 323 313 328 322 580 Liquidus temperature [°c] 1050 1030 1050 1040 1050 1060 >1200 157771.doc -65- s 201231427 Partial dispersion ratio of optical glass of an embodiment of the present invention ( Eg, f) is (-0.00170xvd+0.6375) or more, more specifically, 〇17〇XVd+〇642〇) or more. In particular, the partial dispersion ratio (eg, f) of the optical glass of the examples (N〇_Cl~N〇 C6) was (_0.0017 〇 XVd + 〇 64486) or more. Further, the partial dispersion of the optical glass of the embodiment (No. Al to N〇. A13) of the present invention is more than (-0.0017 〇 XVd + 〇6375 〇), and it is presumed that it has a desired higher portion. Dispersion ratio. On the other hand, the partial dispersion ratio (0g, F) of the optical glass of the embodiment (N〇 bi~n〇 B23) of the present invention is (〇 〇〇 2 〇〇χ to + 0.64982) or more. Therefore, it is clear that the partial dispersion ratio (0g, F) of the relationship between the optical glass system and the Abbe number (vd) of the embodiment of the present invention is large, and the chromatic aberration when forming the optical element is small. The refractive index (nd) of the optical glass of the embodiment of the present invention is 丨57 or more 'more specifically 1.65 or more' and the refractive index (11 < 〇 is 2 2 〇 or less, more specifically 1.85 or less, In particular, the refractive index (nd) of the optical glass of the embodiment (No. A, No. A13) of the present invention is 1.73 or more, and the refractive index (nd) is 丨78 or less. Further, the refractive index (nd) of the optical glass of the embodiment (No. B ^Νο. B23) of the present invention is 1.70 or more, and more specifically L75 or more. Further, the embodiment (n〇Cl~No. C6) The refractive index (nd) of the optical glass is 丨6〇 or more, more specifically 1.65 or more, and the refractive index (nd) is 17〇 or less. Further, the embodiment (No. Dl~No. D36) The refractive index (nd) of the optical glass is 丨 or more, and the refractive index (nd) is 1.81 or less. Further, the Abbe number (~) of the optical glass of the embodiment of the present invention is 39 or more, and more specifically Said to be 40.7 or more, and the Abbe number (Vd) is 63 to 157771.doc -66-201231427 under 'more detailed, 61 or less, within the required range In particular, the Abbe number (Vd) of the optical glass of the embodiment (No. A1 to No. A13) of the present invention is 45 or more 'more specifically 49 or more, and the Abbe number (Vd) 6 Å or less, more specifically 54 or less. Further, the Abbe number (Vd) of the optical glass of the embodiment (No B1 to No. B23) of the present invention is 39 or more, and more specifically 40.7 or more. And the Abbe number (Vd) is less than 52, more specifically 51.3 or less. Further, the Abbe number (vd) of the optical glass of the embodiment (N〇. ci~No. C6) of the present invention is 50 or more, more specifically 54 or more, and the Abbe number (vd) is 57 or less. Further, the Abbe number (Vd) of the optical glass of the embodiment (No. D1 to No. D36) of the present invention is 45 or more, and the Abbe number (vd) is 63 or less, and more specifically 61 or less. Here, in the optical glass of the embodiment (N〇. Cl~No. C6) of the present invention, the present invention The Abbe number (Vd) of the optical glass is such that it satisfies the relationship of (vd)g(-l〇〇xnd+220) with respect to the refractive index (nd). Further, the embodiment of the present invention (No. D1 to No) · D36) glass of optical glass The glass transition point (Tg) is 650 ° C or less 'more specifically 62 〇. 〇 below, within the required range. Also 'specifies the glass transition point (Tg) of the optical glass of other embodiments of the present invention Also, it is 650 ° C or less. Further, in the optical glass of the embodiment (No. D1 to No. D36) of the present invention, 8 〇 (wavelength at a transmittance of 80%) is 5 〇〇 nm or less, more detailed. In terms of 410 nm or less. Further, in the embodiment (N〇m~N〇D36) of the present invention, the optically intelligent person 5 (the wavelength at which the tooth permeability is 5%) is 450 nm or less, and more specifically 350 nm or less, as needed. Within the scope. Further, it is presumed that the kQ (wavelength at the time of transmittance) of the optical glass of the other embodiments of the present invention is also

S 157771.doc -67- 201231427 is below 500 nm 'wavelength at 5% penetration rate) is also below 450 nm. Further, in the optical glass of the present invention (No. D1 to No. D36), the liquidus temperature is 1200 ° C or lower, and more specifically, 11 () 以下 or less, and the liquidus temperature is 500. Above °C. On the other hand, the liquid phase temperature of the glass of the comparative example (ν〇·dl) was 1200 ° C or more. Therefore, it is clear that the optical glass of the embodiment of the present invention has a liquidus temperature lower than that of the glass of the comparative example and is difficult to devitrify. Further, it is estimated that the photoelastic constant (β) of the optical glass system at a wavelength of 546.1 nm in the examples (No. A1 to No. A1 3) of the present invention is 2. 〇xl 〇 -5 nm.cnr1. Pa'1 or less . Therefore, it is clear that the optical glass system refractive index (nd) and the Abbe number (Vd) of the embodiment of the present invention are within a desired range, and the chromatic aberration is small, and it is easy to perform press molding, and the visible region wavelength light is High transparency. In particular, it is also clear that the optical glass of the examples (No. D1 to No. D36) of the present invention has high resistance to devitrification. Further, it is considered that the disordered reflection inside the optical glass-based optical glass of the examples (No. A1 to No. A13) is also small. Further, the optical glass obtained in the examples of the present invention is subjected to re-extrusion molding, and then subjected to grinding and polishing to form a lens and a crucible. Further, the optical glass of the embodiment of the present invention is used to form a preform for precision extrusion molding, and the preform for precision extrusion molding is subjected to precision extrusion molding. In either case, problems such as opalization and devitrification do not occur in the glass which is softened by heating, and it can be stably processed into various lenses and prisms. 157771.doc -68 - 201231427 The above is a detailed description of the present invention, but it is to be understood that the present invention is not limited by the scope of the present invention. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a view showing a partial dispersion ratio (eg, f) as a vertical axis and an Abbe number (νd) as a normal line indicated by orthogonal coordinates of a vehicle.

C 15777I.doc 69-

Claims (1)

201231427 VII. Patent application scope: 1- An optical glass containing B2〇3 component, having a refractive index (nd) of 1.70 or more and an Abbe number (Vd) of 39 or more, and a partial dispersion ratio (0g 'F) is attached to (0g, F)2 (-〇.〇〇17〇xvd+〇.63750) or (〇g,F)g(-2.〇xl〇-3xVd + 〇.6498) is satisfied with the Abbe number (vd) ) relationship. 2. The optical glass of claim 1, further comprising a La203 component having a refractive index (nd) of 丨.73 or more and an Abbe number (vd) of 45 or more, and a partial dispersion ratio (eg 'f) is associated with The relationship between the number of shells (Vd) and F)g (_0 0017〇χ vd+0.63750) is satisfied. 3. The optical glass of claim 1, which further comprises a La2〇3 component and an F component, having an Abbe number (Vd) of 39 or more and less than 52, a partial dispersion ratio, and a lanthanum and an Abbe number (vd) The relationship between (0g, F) 2 (_2. 〇 xl 〇 - 3xVd + 0.6498) is satisfied. 4. The optical glass of claim 1, further comprising an F component having an Ay-square (vd) as an X-axis and an Xy orthogonal coordinate having a refractive index (nd) as a y-axis, having A (50, 1.70), B(6〇,16〇) The Abbe number and the refractive index of the range surrounded by the four points of 'c(63, i 6〇) and D(63, i 7〇). 5. The optical glass according to any one of claims 2 to 4, wherein the content of the ho component is 5. 〇 50.0%, the content of the La 203 component, relative to the total mass of the glass of the oxide conversion composition. It is 55.0% or less. 6. The optical glass according to claim 5, which contains 5.0% or more of the La2〇3 component with respect to the total % by mass of the oxide-converted composition. 7. The optical glass of claim 1, wherein the oxide-converted composition further comprises an Al2?3 component. 157771.doc 201231427 8. 9. 10. 11. 12. 13. 14. 15. : Optical glass of agricultural product 1, which is composed of (4) total mass relative to oxide. /. The content of the 'A] 2〇3 component is 2% or less. In the optical glass of the first item 1, the content of the F component is not more than 3 〇% by mass of the oxide base. The optical glass of h 9 is contained in an amount of more than 〇% of the mass % in the oxide standard. In the optical glass of the term 1 of the moon, the content of the Sic > 2 component is 40% or less by mass% based on the oxide-to-mass composition of the oxide conversion composition. In the optical glass of the item 1 of the present invention, the mass of the total mass of the glass and the composition of (Si〇2+B2〇3) are 40.0% or less. The optical glass of claim 1, wherein the total mass of the glass relative to the oxide-converted composition is, by mass%, Gd2〇3 component 〇40.0% and/or Υ2〇3 component 0 to 20.0% and/or Yb2〇3 The composition 〇~20.0% and/or the Lu2〇3 component 〇~20.0%. The optical glass of claim 1, wherein the Ln2〇3 component of the glass total shell s is equivalent to the composition of the oxide (in the formula, the Ln is selected from the group consisting of La, γ, Yb, and Lu) The mass sum of the above) is 8〇〇% or less. The optical glass of the claim ,, wherein the mass of the total mass of the glass relative to the oxide-converted composition and (Gd2〇3+Yb2〇3) is 26.0% or less. 157771.doc 201231427 16 17. 18. 19. 20. 21. 22. The optical glass of claim 1 wherein the mass ratio in the oxide-converted composition is Ln2〇3/(Bi2〇3+Ti〇2+W〇3 +Nb2〇5+Ta2〇5A i 7 The above is the following. In the optical glass of claim 1, the mass ratio of the oxide conversion composition is Ln203/(Si〇2+B203) is 1.00 or more (in the formula, 'Ln is selected The optical glass of claim 1, which further comprises the total mass of the glass relative to the oxide-converted composition, in terms of mass%, Bi2〇3 composition 0~10.0% and/or Ti〇2 component 0~15.0°/. and/or Nb2〇5 component 0~20.0% and/or w〇3 component 0~15.0% and/or κ2〇 component 〇~10.0% The optical glass of claim 1, wherein the mass of the total mass of the glass relative to the oxide conversion composition and (F+Bi203+Ti02+wc)3+Nb2()5+K2Q) are 0.1% or more and 30.0%. the following. The optical glass of claim 1, wherein the mass of the total mass of the glass relative to the oxide-converted composition and (Bi203 + Ti02 + W03 + Nb 205) are 2 〇 % or less. The optical glass of claim 1, wherein the mass ratio F/(F+Bi203+Ti02+W03+Nb205+K20) in the oxide-converted composition is 0.36 or more and i·〇〇 or less. The optical glass of claim 1, which further comprises, by mass%, 157771.doc 201231427 Zr02 component 0 to 15.0% and/or Ta205 component 0 to 25.0% by mass. The optical glass of claim 1, wherein the mass of the total mass of the glass relative to the oxide-converted composition and (W03 + La203 + Zr02 + Ta205) are 10.0% or more and 60.0% or less. 2. The optical glass of claim 1, wherein the mass of the total mass of the glass relative to the oxide conversion composition (Bi203 + Ti02 + W03 + Nb2 〇 5 + Ta205) is more than 0%. [2] The optical glass of claim 1, wherein the content of the Li20 component is 15.0% or less by mass based on the total mass of the glass of the oxide conversion composition. 26. The optical glass of claim 1, wherein the mass ratio (Ta205 + Zr02 + Li20) / (F + Bi203 + Ti02 + W03 + Nb 205 + K20) in the oxide-converted composition is 2.00 or less. 27. The optical glass of claim 1, wherein the mass ratio of the oxide-converted composition (F + Bi203 + Ti02 + W〇3 + Nb205 + K20) / (Ta205 + Zr02 + Li20) is 0.5 or more. 2. The optical glass of claim 1, which further comprises, by mass%, MgO component 0 to 20.0% and/or CaO component 0-40.0% and/or SrO component, relative to the total mass of the glass in terms of oxide conversion composition. Each component of 0 to 40.0% and/or BaO component 0 to 55.0%. 29. The optical glass of claim 1, wherein the composition is 157771.doc 201231427 201231427 30. 31. 32. 33. 34. 35. 36. 36. 36. 36. 36. 36. The mass of the 'selected from the group consisting of Mg, Ca, Sr, and Ba) is 55 % by mass or less. The optical glass of claim 1, wherein the content of the total mass of the glass in terms of the composition of the oxide is 2j·, and the content of the T Na2 〇 component of the eight persons is 20.0% or less. . For example, the mass of the Rn2〇 component (in the formula, one or more selected from the group consisting of Y, Y, and K) of the optical glass of the composition of the optical fiber of the item 1 is 25.0% or less. The optical glass of claim 1, wherein the content of the Zn0 component is in the range of % by mass or less based on the total mass of the glass of the oxide-converted composition. The optical glass of claim 1, which further comprises, by mass%, Ge?2 component 〇~10.0% and/or p2〇5 component 0~10·0% and/or Or Ga2〇3 component 〇10.0% and/or Te〇2 component 〇10.0% and/or Sn〇2 component 0-5.0% and/or Sb2〇3 component 0-1.0% of each component. The optical glass of claim 1, which has a refractive index (nd) of 1.57 or more and an Abbe number (Vd) of 45 or more. The optical glass of claim 1, wherein the Abbe number (Vd) is in a relationship with the refractive index (nd) satisfying the relationship of vdg - l〇〇xnd + 220. For example, the optical glass of Item 1 wherein the Abbe number (vd) is in a relationship with the refractive index I57771.doc 201231427 (η<ί) satisfies the relationship of vd 2 -125 xnd+265. 37. 38. 39. 40. A preformed body material comprising the optical glass β of claim 1 which is formed by extrusion molding the preformed body of claim 37. An optical element is made of an optical glass as claimed in the claims. - An optical device comprising an optical component as claimed in claim 38 or 39. 157771.doc -6 ·