# Patent

## Title
Optical glass, preform for precision press molding, and optical element

## Abstract

The present invention relates to an optical glass with a high refractive index and good precision press moldability, and a preform for precision press molding and an optical element that are comprised of the optical glass. The present invention further relates to a method of manufacturing an optical element, a lens unit being equipped with an optical element and an image pickup device being equipped with a lens unit.

## Background
CROSS-REFERENCE TO RELATED APPLICATIONS
This application claims benefit of priority to U.S. Provisional Application No. 61/149,493 filed on Feb. 3, 2009, which is expressly incorporated herein by reference in its entirety.


TECHNICAL FIELD
The present invention relates to an optical glass, a preform for precision press molding, and an optical element. More particularly, the present invention relates to an optical glass with a high refractive index and good precision press moldability, and a preform for precision press molding and an optical element that are comprised of the optical glass.
BACKGROUND ART
Correction of chromatic aberration in image pickup optical systems, typified by camera lenses, is achieved by combining a high dispersion lens and a low dispersion lens. In recent years, the trend has been to attempt to achieve greater functionality and compactness through the use of optical lenses with higher refractive indexes for both high and low dispersion lenses within the feasible scope of correction of chromatic aberration.
In addition to manipulating the optical characteristics of the glass constituting a lens, it is also possible to achieve greater functionality and compactness in optical systems by rendering the optical functional surfaces of the lens asymmetric. The precision press molding method is suited to the large-scale production of such lenses.
To improve the productivity of the precision press molding method, it is necessary to first achieve a certain degree of moldability to ensure the productivity of glass materials or preforms for precision press molding. That is, a certain viscosity of glass at a temperature at which crystals do not precipitate, or a certain degree of resistance to devitrification at a temperature at which the glass is of moldable viscosity, is required.
On that basis, it is also necessary to enhance the productivity of precision press molding. Expensive mold materials that are resistant to heat and highly rigid, such as SiC and superhard materials, are employed in the precision press molding method. Pressing molds with molding surfaces that have been precision processed into shapes the reverse of the shapes of the optically functional surfaces of optical elements are employed. As a result, the service lifetime of the pressing mold greatly affects production costs and productivity. Thus, effort has been expended on employing glasses with a low glass transition temperature and sag temperature to lower the temperature during press molding and prevent the thermal deterioration of the pressing mold.
Patent Document 1 discloses an optical glass having a low glass transition temperature (Tg), a high refractive index, low dispersion, and good internal glass quality, that is suited to reheat press molding and/or precision press molding. This optical glass is described as having optical constants within the specific ranges indicated in FIG. 1 of Patent Document 1, a low glass transition temperature (Tg), and good internal glass quality that are achieved by the incorporation of prescribed quantities of SiO2, B2O3, La2O3, Gd2O3, Li2O, and F. Thus it is suited to reheat press molding and/or precision press molding.
The optical glass described in Patent Document 2 is a known optical glass having a composition similar to that described in Patent Document 1. An SiO2—B2O3—La2O3—ZnO—ZrO2—F system optical glass with a high refractive index and low dispersion is disclosed in Patent Document 2. This optical glass is described has having a high refractive index, low dispersion, and good devitrification stability. However, there is no description regarding reheat press molding or precision press molding in Patent Document 2. Patent Document 3 describes an SiO2—B2O3—La2O3—Gd2O3—Li2O—F system low transition temperature (Tg) glass preform material having a high refractive index and low dispersion within a prescribed range for use in precision press molding, and an optical glass suited to precision press molding.

    [Patent Document 1] Japanese patent publication 2005-170782
    [Patent Document 2] Japanese patent publication shou 59-169952
    [Patent Document 3] WO2004/015978
    Patent Documents 1 to 3 are expressly incorporated herein by reference in their entirety


The differences between Patent Documents 1 and 2 are as follows. The optical glass described in Patent Document 1 contains essentially no As2O3, while all the glasses specifically disclosed in Patent Document 2, with but one exception, contain As2O3. In Patent Document 1, As2O3 is eliminated as a component that greatly burdens the environment.
The SiO2—B2O3—La2O3—ZnO—ZrO2—F system optical glasses described in above-cited Patent Documents 1 and 2 are good optical glasses with high refractive indexes and low dispersion. However, the glasses described in Patent Document 1 comprise a relatively large quantity of expensive Yb2O3, or have a high liquidus temperature, which presents problems in terms of moldability. Many of the glasses disclosed as examples have glass transition temperatures exceeding 600° C., and are not necessarily suitable as optical glasses for precision press molding. The optical glasses of Patent Document 2 have a high glass transition temperature, and cannot be considered suitable for precision press molding. The optical glasses described in above-cited Patent Document 3 present such problems as inadequate thermal stability.
Accordingly, an object of the present invention is to provide an optical glass that solves the above problems and is suited to precision press molding.
SUMMARY OF THE INVENTION
The optical glass of the present invention is comprised of two basic forms specified from different perspectives.
The first basic form of the present invention provides an optical glass having a high refractive index and low dispersion characteristics, exhibiting good thermal stability, with a low glass transition temperature, that is suited to precision press molding.
The optical glass of the first basic form of the present invention is an optical glass characterized by comprising, denoted as cationic percentages,

















BO1.5
20 to 70
percent;



LaO1.5
6 to 30
percent;



GdO1.5
4 to 25
percent;










as well as O and F, with the F/O molar ratio of the F content to the O content being 0.01 to 0.30.

The second basic form provides a high quality optical glass containing B, O, and F as components, volatizing little in melt form, and having characteristics such as optical characteristics that vary little.
The optical glass of the second basic form of the present invention is an optical glass comprising glass components in the form of cations including B and anions including O and F, wherein the value of BB—(BO—BB) falls within a range of −60 to +60, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO.
The present invention further comprises four forms, denoted by A to D below, that are included in the first and second basic forms. The four forms of A to D relate to optical glasses that satisfy the conditions of the above-described first and second basic forms and have refractive indexes nd and Abbé numbers ν(nu)d that lie in mutually different regions.
The optical glass of Form A is an optical glass comprising,
denoted as cationic percentages:

















BO1.5
20 to 70
percent;



LaO1.5
6 to 30
percent;



GdO1.5
4 to 25
percent;



SiO2
0 to 20
percent;



LiO0.5
0 to 20
percent;



ZnO
0 to 20
percent;



ZrO2
0 to 4.5
percent;



TaO2.5
0 to 7
percent;



YbO1.5
0 to 0.5
percent;



GeO2
0 to 5
percent;










as well as O and F,

with the F/O molar ratio of the F content to the O content being 0.01 to 0.30;
the combined sum of the ZnO content, three times the ZrO2 content, and five times the TaO2.5 content (ZnO+3ZrO2+5TaO2.5) being 40 percent or less;
the combined sum of twice the LiO0.5 content, the ZnO content, and 1⁄2 the F content (2LiO0.5+ZnO+(F/2)) when the total quantity of cations is denoted as 100 being 20 percent or greater;
the value of BB—(BO—BB) falling within a range of −60 to +20, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO;
the refractive index nd being 1.75 to 1.81; and
the Abbé number νd being 48 to 52.
The optical glass of Form B is an optical glass comprising,
denoted as cationic percentages:

















BO1.5
20 to 70
percent;



LaO1.5
6 to 30
percent;



GdO1.5
4 to 25
percent;



SiO2
0 to 20
percent;



LiO0.5
0 to 20
percent;



ZnO
0 to 25
percent;



ZrO2
8
percent or less;



TaO2.5
7
percent or less;



YbO1.5
0 to 3
percent;



GeO2
0 to 5
percent;










as well as O and F,

with the F/O molar ratio of the F content to the O content being 0.01 to 0.30;
the ratio of the ZrO2 content to the combined content of ZrO2 and TaO2.5(ZrO2/(ZrO2+TaO2.5)) being 0 to 0.7;
the combined sum of ZrO2 and TaO2.5(ZrO2+TaO2.5) being 3 to 10;
the combined sum of twice the LiO0.5 content, the ZnO content, and 1⁄2 the F content (2LiO0.5+ZnO+(F/2)) when the total quantity of cations is denoted as 100 being 20 percent or greater;
the value of BB—(BO—BB) falling within a range of −60 to +20, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO;
the refractive index nd being 1.79 to 1.835; and
the Abbé number νd being 42 to 48.
The optical glass of Form C is an optical glass comprising,
denoted as cationic percentages:

















BO1.5
20 to 70
percent;



LaO1.5
6 to 30
percent;



GdO1.5
4 to 25
percent;



SiO2
0 to 20
percent;



LiO0.5
0 to 20
percent;



ZnO
0 to 15
percent;



ZrO2
5
percent or less;



TaO2.5
3
percent or less;



YbO1.5
0 to 3
percent;



GeO2
0 to 5
percent;










as well as O and F,

with the F/O molar ratio of the F content to the O content being 0.01 to 0.30;
the combined sum of the ZnO content, three times the ZrO2 content, and five times the TaO2.5 content (ZnO+3ZrO2+5TaO2.5) being 15 percent or less;
the combined sum of twice the LiO0.5 content, the ZnO content, and 1⁄2 the F content (2LiO0.5+ZnO+(F/2)) when the total quantity of cations is denoted as 100 being 20 percent or greater;
the value of BB—(BO—BB) falling within a range of −60 to +60, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO;
the refractive index nd being 1.675 to 1.76; and
the Abbé number νd being 51 to 58.
The optical glass of Form D is an optical glass comprising,
denoted as cationic percentages:

















BO1.5
20 to 70
percent;



LaO1.5
6 to 30
percent;



GdO1.5
4 to 25
percent;



SiO2
0 to 20
percent;



LiO0.5
0 to 10
percent;



ZnO
0 to 28
percent;



ZrO2
0 to 8
percent;



TaO2.5
0 to 10
percent;



TiO2
0 to 8
percent;



NbO2.5
0 to 8
percent;



WO3
0 to 10
percent;



YbO1.5
0 to 3
percent;



GeO2
0 to 5
percent;










as well as O and F,

with the F/O molar ratio of the F content to the O content being 0.01 to 0.30;
the combined sum of twice the LiO0.5 content, the ZnO content, and 1⁄2 the F content (2LiO0.5+ZnO+(F/2)) when the total quantity of cations is denoted as 100 being 20 percent or greater;
the value of BB—(BO—BB) falling within a range of −60 to 0, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO;
the refractive index nd being 1.825 to 1.90; and
the Abbé number νd being 35 to 43.
The first basic form of the present invention provides an optical glass characterized by having a high refractive index, low dispersion, good thermal stability, and a low glass transition temperature, that is suited to precision press molding. The second basic form of the present invention provides a quality optical glass comprising glass components in the form of B, O, and F, with little volatility in a melted state, that exhibits little variation in characteristics such as optical characteristics.
The four forms A to D of the present invention provide optical glasses that satisfy the conditions of the first and second basic forms. Thus, they exhibit the effects of the invention that are found in the first and second basic forms of the present invention, while additionally having the refractive indexes nd and Abbé numbers νd corresponding to their individual forms.
Form A of the present invention provides an optical glass having a refractive index nd of 1.75 to 1.81 and an Abbé number of 48 to 52; Form B of the present invention provides an optical glass having a refractive index nd of 1.79 to 1.835 and an Abbé number of 42 to 48; Form C of the present invention provides an optical glass having a refractive index nd of 1.675 to 1.76 and an Abbé number of 51 to 58; and Form D of the present invention provides an optical glass having a refractive index nd of 1.825 to 1.90 and an Abbé number of 35 to 43, respectively.



BRIEF DESCRIPTION OF THE DRAWINGS
FIG. 1 The numeric values recorded near the various plots in FIG. 1 denote the melting time in unit of hours.
FIG. 2 shows the change in the refractive indexes of Examples 32 and 33 in Table 3 (Form A), with the horizontal axis denoting the melting time and the vertical axis denoting the refractive index nd.
FIG. 3 shows the change in specific gravity of Examples 32 and 33 in Table 3 (Form A), with the horizontal axis denoting the melting time and the vertical axis denoting specific gravity.
FIG. 4 shows the change in the glass transition temperature of Example 32 in Table 3 (Form A), with the horizontal axis denoting the melting time and the vertical axis denoting the glass transition temperature Tg.
FIG. 5 shows the change in Tg resulting from change in 2LiO0.5+ZnO+(F/2), with the horizontal axis denoting the value of 2LiO0.5+ZnO+(F/2) and the vertical axis denoting the glass transition temperature Tg.
FIG. 6 shows change in the inverse of kinematic viscosity and change in viscosity corresponding to change in temperature in an example (Example 8 (nd=1.72686, νd=54.41) of Form C (Table 5)) of the optical glass of the present invention, with the horizontal axis denoting temperature, the left vertical axis denoting the viscosity of the glass, and the right vertical axis denoting the inverse of kinematic viscosity, an index of the flow rate.
FIG. 7 shows microscopic photographs of the various glasses, following holding, in the comparative examples.
FIG. 8 shows the results (photographs) of a comparison experiment of wet backwordly.
FIG. 9 shows transmittance curves for glasses reproduced from Patent Documents 1 and 3.
FIG. 10 shows change in weight reduction (volatilization) due to change in the F content for optical glasses of the present invention of Forms A to D, with the horizontal axis denoting the F content and the vertical axis denoting change in weight.
FIG. 11 shows the relation between the D value and the change in weight for glasses having an F content of 7 to 9 percent, with the horizontal axis denoting the D value and the vertical axis denoting change in weight.
FIG. 12 shows the relation between the D value and the change in weight for glasses having an F content of 14 to 16 percent, with the horizontal axis denoting the D value and the vertical axis denoting change in weight.
FIG. 13 is a combination of FIGS. 11 and 12.



MODES FOR CARRYING OUT THE INVENTION
The optical glass of the present invention is described in greater detail below.
The optical glass of the first basic form and the optical glass of the second basic form of the present invention share the fact that they comprise the glass components of B as a cation and O and F as anions. There are thus cases where their compositions and physical properties overlap. That is, the optical glass of the first basic form can satisfy the conditions prescribed for the optical glass of the second basic form, and the optical glass of the second basic form can satisfy the conditions prescribed for the optical glass of the first basic form.
Tables 1-1 to 1-29 and 2-1 to 2-18 give desirable composition ranges and desirable characteristics for the optical glass of the first basic form. An optical glass having any combination of the composition ranges and characteristic ranges indicated in these tables is possible in the present invention.
Any optical glass optionally combining a composition range and a characteristic range given in any of Tables 1-1 to 1-29 and 2-1 to 2-18 corresponds to desirable optical glass of the second basic form.
Tables 1-1 to 1-29 and 2-1 to 2-18 record desirable composition ranges and desirable characteristics for the four forms of A to D. For Forms A to D, any combination of desirable forms of the first form and the second form is possible so long as it falls within the range of one of the forms.
As set forth above, Form A is a glass that is suited to realizing optical constants in the form of a refractive index nd of 1.75 to 1.81 and an Abbé number νd of 48 to 52.
The fact that Form A, as denoted by cationic percentages, is an optical glass comprising:

















BO1.5 
20 to 70
percent;



LaO1.5
6 to 30
percent;



GdO1.5
4 to 25
percent;










as well as O and F, with the F/O molar ratio of the F content to the O content being 0.01 to 0.30, is shared with optical glasses of the first basic form of the present invention. These compositions will be described further below with reference to Tables 1 and 2. Satisfying these conditions yields an optical glass having characteristics of a high refractive index and low dispersion, good thermal stability, and a low glass transition temperature that is suited to precision press molding.

Further, the fact that Form A is an optical glass comprising the glass components of cations including B and anions including O and F, and an optical glass in which the value of BB—(BO—BB) falls within a range of −60 to +60, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO, is shared with optical glasses of the second basic form of the present invention. Satisfying these conditions yields a quality optical glass comprising glass components in the form of B, O, and F, with little volatilization in a melted state, exhibiting little variation in various characteristics such as optical characteristics. However, in Form A, the upper limit of BB—(BO—BB) is +20. The reasons for this are as follows. In Form A, when large numbers of components with high melting points, such as rare earth components, Zr, and Ta, are included among the glass components to increase the refractive index, the liquidus temperature increases and the temperature at which the glass flows out tends to rise. Accordingly, this upper limit, an indicator of the ratio of volatilizable bonding in the present glass system, is set to inhibit volatilization of glass components at relatively high temperatures.
The fact that

















SiO2
0 to 20
percent;



LiO0.5
0 to 20
percent;



ZnO
0 to 20
percent; and



GeO2
0 to 5
percent










are also incorporated is shared with optical glasses of the first and second basic forms of the present invention. A description of these compositions will be given further below with reference to Tables 1 and 2.

The fact that

















ZrO2
0 to 4.5 
percent;



TaO2.5
0 to 7
percent; and



YbO1.5
0 to 0.5
percent










are incorporated differs from the optical glasses of the first and second basic forms of the present invention.

ZrO2 is set to 0 to 4.5 percent because when the ZrO2 content exceeds 4.5 percent, the dispersion tends to increase and the liquidus temperature tends to rise. The upper limit of the ZrO2 content is desirably 3.8 percent, preferably 3.4 percent, more preferably 3 percent, still more preferably 2.7 percent, and yet more preferable upper limit is 2.5 percent.
TaO2.5 is set to 0 to 7 percent because when the content of TaO2.5 exceeds 7 percent, it becomes difficult to maintain desired dispersion and good stability. The upper limit of the TaO2.5 content is desirably 5 percent or lower, preferably 4 percent or lower, more preferably 3 percent, still more preferably 2 percent, yet more preferably 1.5 percent, and even more preferably, 1.2 percent. The lower limit of the TaO2.5 content is desirably 0.1 percent, preferably 0.3 percent, more preferably 0.5 percent, and still more preferably, 0.6 percent.
ZrO2 is one of the glass starting materials that melts the most poorly and requires a high temperature for homogenization. This causes the volatilization of a large amount of fluorine in the process of melting and homogenizing the starting materials of the glass of the present invention, which include fluorine. Thus, the incorporation of large quantities of this component is undesirable from the perspective of suppressing the variation in glass characteristics that accompany volatilization.
YbO1.5 is set to 0 to 0.5 percent because of high cost and because the incorporation of an excessive quantity increases the liquidus temperature, indirectly fostering the volatilization of glass components and compromising the homogeneity and molding characteristics of the glass. Further, this component absorbs radiation in the infrared region, rendering the glass unsuitable for use in highly sensitive optical systems of which sensitivity characteristics in the near infrared range are required, such as high-precision video cameras and surveillance cameras. In particular, the optical lens of Form A is suited to the greatest range of optical design applications among all of the forms. To permit use in these optical systems, the quantity of YbO1.5 is desirably limited.
(ZnO+3ZrO2+5TaO2.5) is set to 40 percent or less to maintain low dispersion. (2LiO0.5+ZnO+(F/2)) is set to 20 percent or more to lower the (maintain a low) glass transition temperature.
In particular, as set forth above, Form A is an optical glass having optical constants in the form of a refractive index nd of 1.75 to 1.81 and an Abbé number νd of 48 to 52. Thus, to obtain an optical glass satisfying both this refractive index nd and Abbé number νd, it suffices to divide the glass components into the following categories and adjust the contents thereof. That is, it suffices to adjust: (1) the total quantity NWF of glass forming components, such as BO1.5, SiO2, and AlO1.5, an increase in the content of which has the effect of reducing the refractive index and increasing the Abbé number; (2) the total quantity Σ(SIGMA)RE of rare earth components, such as LaO1.5, GdO1.5, and YO1.5, an increase in the content of which has the effect of increasing the refractive index and slightly reducing the Abbé number, thereby increasing the refractive index and lowering the dispersion of the glass; (3) the total quantity (ZrO2+TaO2.5) of components, such as ZrO2 and TaO2.5, an increase in the content of which has the effect of greatly increasing the refractive index and slightly reducing the Abbé number; (4) the total quantity of high refractive index, high dispersion elements, such as TiO2, NbO2.5, WO3, and BiO1.5, an increase in the content of which has the effect of greatly increasing the refractive index and greatly reducing the Abbé number; (5) the total quantity of monovalent and divalent components, such as LiO0.5 and ZnO, an increase in the content of which has the effects of lowering the melting temperature of the glass starting materials, enhancing the stability of the glass, lowering the liquidus temperature, lowering the glass transition temperature, and the like; and (6) the total quantity of components other than those listed above. Among these, the adjustment of (1) to (4) above is effective for adjusting optical characteristics.
Specifically, the following applies for important components (1) to (3) of the present invention. The upper limit of (1) NWF is desirably 63 percent, preferably 60 percent, more preferably 58 percent, still more preferably 57 percent, still more preferably 56 percent, still more preferably 55 percent, and yet more preferably, 54 percent. Additionally, the lower limit of NWF is desirably 41 percent, preferably 44 percent, more preferably 46 percent, still more preferably 47 percent, still more preferably 48 percent, still more preferably 49 percent, and yet more preferably, 50 percent. The upper limit of (2) ΣRE is desirably 38 percent, preferably 36 percent, more preferably 35 percent, still more preferably 34 percent, still more preferably 33 percent, still more preferably 32 percent, and yet more preferably, 31 percent. Additionally, the lower limit of ΣRE is desirably 20 percent, preferably 22 percent, more preferably 23 percent, still more preferably 24 percent, still more preferably 25 percent, still more preferably 26 percent, and yet more preferably, 27 percent. The upper limit of (3) (ZrO2+TaO2.5) is desirably 8 percent, preferably 7 percent, more preferably 6 percent, still more preferably 5 percent, still more preferably 4.5 percent, still more preferably 4 percent, and yet more preferably, 3.5 percent. Additionally, the lower limit of (ZrO2+TaO2.5) is desirably 0 percent, preferably 1 percent, more preferably 2 percent, still more preferably 2.5 percent, and yet more preferably, 3 percent.
The quantities of ΣRE and NWF can be adjusted by referencing the ratio of ΣRE and NWF, namely, ΣRE/NWF. The upper limit of ΣRE/NWF is desirably 0.9, preferably 0.85, still more preferably 0.80, still more preferably 0.75, still more preferably 0.70, still more preferably 0.65, and yet more preferably, 0.60. Additionally, the lower limit of ΣRE/NWF is desirably 0.50, preferably 0.45, more preferably 0.40, still more preferably 0.35, and yet more preferably, 0.30.
Additional conditions are as follows. To lower the liquidus temperature by mixing rare earth components, thereby raising (maintaining) the stability of a glass with relatively good optical characteristics, it is desirable to pay attention to the ratio of LaO1.5 to the total quantity of rare earth elements ΣRE, namely LaO1.5/ΣRE. In Form A, which has the above-described desirable component structure, the upper limit of LaO1.5/ΣRE is desirably 0.75, preferably 0.7, more preferably 0.65, still more preferably 0.6, still more preferably 0.57, still more preferably 0.55, still more preferably 0.53, and yet more preferably, 0.52. Additionally, the lower limit of LaO1.5/ΣRE is desirably 0.30, preferably 0.4, more preferably 0.45, still more preferably 0.48, and yet more preferably, 0.49.
In particular, in Form A, in addition to essential rare earth components, it is desirable to preferentially incorporate Zr and Ta from among the high refractive index and high dispersion elements of Zr, Ta, Ti, Nb, W, and Bi. It is preferable to preferentially employ Zr over Ta to achieve both a high refractive index and low dispersion. Thus, optimization of the quantity of Zr incorporated in Form A is extremely effective for enhancing the optical characteristics and molding properties of the glass.
TiO2 and NbO2.5 can be further incorporated into Form A as optional components. TiO2 and NbO2.5 function to increase the refractive index while maintaining low dispersion. However, since they also increase dispersion, TiO2 is set to 0 to 3 percent and NbO2.5 to 0 to 3 percent.
Other high refractive index and high dispersion components can be incorporated to the extent that the effect of the present invention is not spoiled. The upper limit of the total quantity of high refractive index and high dispersion components such as TiO2, NbO2.5, WO3, and BiO1.5 is desirably 6 percent, preferably 5 percent, more preferably 4 percent, still more preferably 3 percent, still more preferably 2 percent, and yet more preferably, 1 percent. Optimally, they are not incorporated at all.
The incorporation of 2 percent or more of SiO2 and maintenance of the ratio (SiO2/BO1.5) at 0.10 or higher are desirable in Form A. This makes it possible to increase the viscosity of the glass melt and enhances the inhibition of striae during molding.
The refractive index nd and the Abbé number νd in Form A desirably satisfy equation (1) below. The relation between the refractive index nd and the Abbé number νd is described further below.

nd−(2.25−0.01×νd)≧−0.01  (1)

Form B is a glass suited to realizing optical constants in the form of a refractive index nd of 1.79 to 1.835 and an Abbé number νd of 42 to 48.
The facts that Form B is an optical glass comprising, denoted as cationic percentages:

















BO1.5 
20 to 70
percent;



LaO1.5
6 to 30
percent;



GdO1.5
4 to 25
percent;










as well as O and F, and that the F/O molar ratio of the F content to the O content is 0.01 to 0.30, are shared with optical glass of the first basic form of the present invention. A description of these compositions will be given further below with reference to Tables 1 and 2. Satisfying these conditions yields an optical glass having high refractive index and low dispersion characteristics, good thermal stability, and a low glass transition temperature, that is suited to precision press molding.

The fact that Form B is an optical glass comprising glass components in the form of cations including B and anions including O and F, such that the value of BB—(BO—BB) falls within a range of −60 to +60, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO, is shared with the optical glass of the second basic form of the present invention. Satisfying these conditions yields a quality optical glass containing glass components in the form of B, O, and F, that undergoes little volatilization in a melted state and exhibits little variation in various characteristics such as optical characteristics. However, in Form B, the upper limit of BB—(BO—BB) is +20. The reason for this is as follows. To raise the refractive index of Form B relative to that of Form C, large quantities of components with high melting points, such as rare earth elements, Zr, and Ta, are included among the glass components. This increases the liquidus temperature, and causes the temperature at which the glass flows out to increase. Accordingly, an upper limit, indicating the ratio of volatilizable bonding in the glass system, is set to inhibit volatilization of glass components at relatively high temperatures.
The fact of comprising

















SiO2
0 to 20
percent;



LiO0.5
0 to 20
percent; and



GeO2
0 to 5
percent










is also shared with the optical glasses of the first and second basic forms of the present invention. The compositions thereof will be described further below with reference to Tables 1 and 2.

The fact of comprising

















ZnO
0 to 25
percent;



ZrO2
8
percent or less;



TaO2.5
7
percent or less; and



YbO1.5
0 to 3 
percent










is a difference with the optical glasses of the first and second basic forms of the present invention.

ZnO is set to 0 to 25 percent because although the introduction of a large quantity of ZnO increases the refractive index somewhat in terms of optical characteristics, there is a problem in that dispersion increases (νd decreases). However, the object of Form B is to obtain a glass having a higher refractive index and a greater dispersion range than Form A, namely nd=1.79 to 1.835 and νd=42 to 48. Thus, the content permitted is greater than in the glass of Form A.
Both ZrO2 and TaO2.5 are components that raise the refractive index. The incorporation of suitable quantities thereof stabilizes the glass, lowers the liquidus temperature, and increases the viscosity of the glass melt. The quantity of ZrO2 is set to 8 percent or less because when the content of ZrO2 exceeds 8 percent, the liquidus temperature tends to increase. The upper limit of the ZrO2 content is desirably 7 percent, preferably 6 percent, more preferably 5 percent, still more preferably 4.5 percent, and yet more preferably, 4 percent. The lower limit of the ZrO2 content is desirably 0.5 percent, preferably 1 percent, and more preferably, 1.5 percent.
TaO2.5 is set to 7 percent or less because when the content of TaO2.5 exceeds 7 percent, it becomes difficult to maintain the desired dispersion and good stability. The upper limit of the TaO2.5 content is desirably 6 percent or less, preferably 5 percent. The lower limit of the TaO2.5 content is desirably 0.1 percent, preferably 0.3 percent, more preferably 0.5 percent, still more preferably 0.6 percent, still more preferably 1 percent, still more preferably 1.5 percent, still more preferably 1.8 percent, and yet more preferably, 2 percent.
YbO1.5 is set to 0 to 3 percent because of high cost and because the introduction of an excessive quantity increases the liquidus temperature, indirectly fostering volatilization of glass components and compromising the homogeneity and molding properties of the glass. Further, this component absorbs radiation in the infrared region, rendering the glass unsuitable for use in highly sensitive optical systems of which sensitivity characteristics in the near infrared range are required, such as high-precision video cameras and surveillance cameras. However, since the glass of Form B has a high refractive index, it can be effectively limited to applications such as compact digital cameras that do not receive light in the infrared range. Thus, YbO1.5 can be incorporated to an upper limit of 3 percent.
(ZrO2/(ZrO2+TaO2.5)) is limited to from 0 to 0.7 to optimize the distribution of Zr and Ta employed in Form B and lower the liquidus temperature, thereby yielding a highly stable glass. (ZrO2+TaO2.5) is set to 3 to 10 to achieve a higher refractive index by using more Zr and Ta than in Form A. The total quantity of (2LiO0.5+ZnO+(F/2)) is set to 20 percent or more to lower the (keep a low) glass transition temperature.
To further improve the stability of the glass and lower the liquidus temperature in Form B, (ZrO2/(ZrO2+TaO2.5)) is desirably limited to 0.7 or lower. From the perspectives of improving the stability of the glass and lowering the liquidus temperature, the upper limit of (ZrO2/(ZrO2+TaO2.5)) is desirably 0.6, preferably 0.55, more preferably 0.50, and still more preferably, 0.45.
The lower limit of (ZrO2/(ZrO2+TaO2.5)) is desirably 0.00, preferably 0.10, more preferably 0.20, still more preferably 0.25, still more preferably 0.30, and yet more preferably, 0.35.
Instead of the above indicators, in glasses containing TaO2.5, (ZrO2/TaO2.5) is desirably limited to 2.5 or lower. From the perspectives of improving glass stability and lowering the liquidus temperature, the upper limit of (ZrO2/TaO2.5) is desirably 1.8, preferably 1.6, more preferably 1.4, still more preferably 1.3, still more preferably 1.2, and yet more preferably, 1.1. The lower limit of (ZrO2+TaO2.5) is desirably 0.1, preferably 0.2, more preferably 0.3, still more preferably 0.4, and yet more preferably, 0.5.
In particular, as set forth above, since Form B is an optical glass having optical constants in the form of a refractive index nd of 1.79 to 1.835 and an Abbé number νd of 42 to 48, to achieve an optical glass achieving both this refractive index nd and Abbé number νd, it suffices to classify the glass components as follows in the same manner as in Form A and adjust their contents. That is, it suffices to adjust: (1) the total quantity NWF of glass forming components, such as BO1.5, SiO2, and AlO1.5, an increase in the content of which has the effect of reducing the refractive index and increasing the Abbé number; (2) the total quantity ΣRE of rare earth components, such as LaO1.5, GdO1.5, and YO1.5, an increase in the content of which has the effect of increasing the refractive index and slightly reducing the Abbé number, thereby increasing the refractive index and lowering the dispersion of the glass; (3) the total quantity (ZrO2+TaO2.5) of components, such as ZrO2 and TaO2.5, an increase in the content of which has the effect of greatly increasing the refractive index and slightly reducing the Abbé number; (4) the total quantity of high refractive index, high dispersion elements, such as TiO2, NbO2.5, WO3, and BiO1.5, an increase in the content of which has the effect of greatly increasing the refractive index and greatly reducing the Abbé number; (5) the total quantity of monovalent and divalent components, such as LiO0.5 and ZnO, an increase in the content of which has the effects of lowering the melting temperature of the glass starting materials, enhancing the stability of the glass, lowering the liquidus temperature, lowering the glass transition temperature, and the like; and (6) the total quantity of components other than those listed above. Among these, the adjustment of (1) to (4) above is effective for adjusting optical characteristics.
Specifically, the following applies for important components (1) to (3) of the present invention. The upper limit of (1) NWF is desirably 60 percent, preferably 57 percent, more preferably 55 percent, still more preferably 54 percent, still more preferably 53 percent, still more preferably 52 percent, and yet more preferably, 51 percent. Additionally, the lower limit of NWF is desirably 35 percent, preferably 38 percent, more preferably 40 percent, still more preferably 41 percent, still more preferably 42 percent, still more preferably 43 percent, and yet more preferably, 44 percent. The upper limit of (2) ΣRE is desirably 42 percent, preferably 40 percent, more preferably 38 percent, still more preferably 37 percent, still more preferably 36 percent, still more preferably 35 percent, and yet more preferably, 34 percent. Additionally, the lower limit of ΣRE is desirably 20 percent, preferably 22 percent, more preferably 23 percent, still more preferably 25 percent, still more preferably 27 percent, still more preferably 28 percent, still more preferably 29 percent, and yet more preferably, 30 percent. The upper limit of (3) (ZrO2+TaO2.5) is desirably 10 percent, preferably 9 percent, more preferably 8 percent, still more preferably 7.5 percent, still more preferably 7 percent, still more preferably 6.5 percent, and yet more preferably, 6 percent. Additionally, the lower limit of (ZrO2+TaO2.5) is desirably 3 percent, preferably 3.5 percent, more preferably 4.0 percent, still more preferably 4.5 percent, and yet more preferably, 5.0 percent.
The quantities of ΣRE and NWF can be adjusted by referencing the ratio of ΣRE and NWF, namely, ΣRE/NWF. The upper limit of ΣRE/NWF is desirably 1.2, preferably 1.1, more preferably 1.0, still more preferably 0.95, still more preferably 0.9, still more preferably 0.85, and yet more preferably, 0.8. Additionally, the lower limit of ΣRE/NWF is desirably 0.35, preferably 0.40, more preferably 0.45, more preferably 0.50, still more preferably 0.55, still more preferably 0.60, and yet more preferably, 0.65.
Additional conditions are as follows. To lower the liquidus temperature by mixing rare earth components, thereby raising (maintaining) the stability of a glass with relatively good optical characteristics, it is desirable to pay attention to the ratio of LaO1.5 to the total quantity of rare earth elements ΣRE, namely LaO1.5/ΣRE. In Form B, which has the above-described desirable component structure into which suitable quantities of Zr and Ta have been introduced in this manner, a ratio in which a large amount of La is employed is effective. That is, the upper limit of LaO1.5/ΣRE is desirably 0.8, preferably 0.75, more preferably 0.70, still more preferably 0.67, still more preferably 0.65, still more preferably 0.63, and yet more preferably, 0.62. Additionally, the lower limit of LaO1.5/ΣRE is desirably 0.30, preferably 0.4, more preferably 0.45, still more preferably 0.5, still more preferably 0.55, still more preferably 0.58, and yet more preferably, 0.59.
In particular, in Form B, in addition to essential rare earth components, it is desirable to preferentially incorporate Zr and Ta from among the high refractive index and high dispersion elements of Zr, Ta, Ti, Nb, W, and Bi. It is desirable to incorporate an optimal quantity of Zr while optimizing the content of Ta to achieve a higher refractive index and higher dispersion than in Form A. Thus, optimization of the quantities and ratio of Ta and Zr incorporated in Form B is extremely effective for enhancing the optical characteristics and molding properties of the glass.
TiO2 and NbO2.5 can be further incorporated into Form B as optional components. TiO2 and NbO2.5 function to increase the refractive index while maintaining low dispersion. However, since they also increase dispersion, TiO2 is set to 0 to 3 percent and NbO2.5 to 0 to 3 percent.
Other high refractive index and high dispersion components can be incorporated to the extent that the effect of the present invention is not spoiled. The upper limit of the total quantity (TiO2+NbO2.5+WO3+BiO1.5) of high refractive index and high dispersion components such as TiO2, NbO2.5, WO3, and BiO1.5 is desirably 8 percent, preferably 6 percent, more preferably 5 percent, still more preferably 4 percent, still more preferably 3 percent, still more preferably 2 percent, and yet more preferably, 1 percent. Optimally, to achieve low dispersion, they are not incorporated at all.
In Form B, it is desirable for (2LiO0.5+ZnO+(F/2)) to constitute 20 percent or more to lower the glass transition temperature.
In the optical glass of Form B, the refractive index nd and the Abbé number νd desirably satisfy equation (2) below. The relation between the refractive index nd and the Abbé number νd is described further below.

nd−(2.25−0.01×νd)≧−0.01  (2)

Form C is a glass that is suited to realizing optical constants in the form of a refractive index nd of 1.675 to 1.76 and an Abbé number νd of 51 to 58.
The fact that Form C, as denoted by cationic percentages, is an optical glass comprising:

















BO1.5 
20 to 70
percent;



LaO1.5
6 to 30
percent;



GdO1.5
4 to 25
percent;










as well as O and F, with the F/O molar ratio of the F content to the O content being 0.01 to 0.30, is shared with optical glasses of the first basic form of the present invention. These compositions will be described further below with reference to Tables 1 and 2. Satisfying these conditions yields an optical glass characterized by a high refractive index, low dispersion, good thermal stability, and a low glass transition temperature, that is suited to precision press molding.

Further, the fact that Form C is an optical glass comprising the glass components of cations including B and anions including O and F, and an optical glass in which the value of BB—(BO—BB) falls within a range of −60 to +60, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO, is shared with optical glasses of the second basic form of the present invention. Satisfying these conditions yields a quality optical glass comprising glass components in the form of B, O, and F, with little volatilization in a melted state, exhibiting little variation in various characteristics such as optical characteristics.
The fact that

















SiO2
0 to 20
percent;



LiO0.5
0 to 20
percent; and



GeO2
0 to 5
percent










are also incorporated is shared with optical glasses of the first and second basic forms of the present invention. A description of these compositions will be given further below with reference to Tables 1 and 2.

The fact that

















ZrO2
5
percent or less;



TaO2.5
3
percent or less; and



YbO1.5
0 to 3 
percent










are incorporated differs from the optical glasses of the first and second basic forms of the present invention.

ZnO is set to 0 to 15 percent because when the ZnO content exceeds 15 percent, dispersion tends to increase, stability decreases, and the liquidus viscosity tends to diminish. The upper limit of the ZnO content is desirably 15 percent, preferably 10 percent, more preferably 8 percent, still more preferably 6 percent, still more preferably 4 percent, still more preferably 3 percent, and yet more preferably, 2 percent. The lower limit of the ZnO content is desirably 0 percent, preferably 0.5 percent, and more preferably, 1 percent. Thus, 2LiO0.5/(2LiO0.5+ZnO), which serves as a yardstick in the adjustment of components lowering the Tg, naturally assumes a somewhat high value. That is, the lower limit of 2LiO0.5/(2LiO0.5+ZnO) is desirably 0.65, preferably 0.7, more preferably 0.75, still more preferably 0.8, still more preferably 0.85, still more preferably 0.9, yet more preferably 0.95 and particularly preferably, 1.00.
ZrO2 is set to 5 percent or less because when the ZrO2 content exceeds 5 percent, dispersion tends to increase and the liquidus temperature tends to rise. The upper limit of the ZrO2 content is desirably 5 percent, preferably 4 percent, more preferably 3 percent, still more preferably 2.5 percent, still more preferably 2 percent, still more preferably 1.5 percent, still more preferably 1 percent, and yet more preferably 0.5 percent. Optimally, no ZrO2 is incorporated at all.
TaO2.5 is set to 3 percent or less because when the content of TaO2.5 exceeds 3 percent, it becomes difficult to maintain desired dispersion and good stability, and the cost of the starting materials increases. The upper limit of the TaO2.5 content is desirably 3 percent or lower, preferably 2 percent, more preferably 1 percent, and yet more preferably, 0.5 percent. Optimally, no TaO2 is incorporated at all.
YbO1.5 is set to 0 to 3 percent because of high cost. Further, this component absorbs radiation in the infrared region, rendering the glass unsuitable for use in highly sensitive optical systems of which sensitivity characteristics in the near infrared range are required, such as high-precision video cameras and surveillance cameras. In particular, the optical glass of Form C can be of lower dispersion than that of Form A and the low dispersion of YBO1.5 can be utilized to prepare a low-dispersion glass in which, for example, νd=55 or higher. Thus, YbO1.5 can be incorporated up to a maximum of 3 percent.
In particular, as set forth above, Form C is an optical glass having optical constants in the form of a refractive index nd of 1.675 to 1.76 and an Abbé number νd of 51 to 58. Thus, to obtain an optical glass satisfying both this refractive index nd and Abbé number νd, it suffices to divide the glass components into the following categories in the same manner as in Form A and adjust the contents thereof. That is, it suffices to adjust: (1) the total quantity NWF of glass forming components, such as BO1.5, SiO2, and AlO1.5, an increase in the content of which has the effect of reducing the refractive index and increasing the Abbé number; (2) the total quantity ΣRE of rare earth components, such as LaO1.5, GdO1.5, and YO1.5, an increase in the content of which has the effect of increasing the refractive index and slightly reducing the Abbé number, thereby increasing the refractive index and lowering the dispersion of the glass; (3) the total quantity (ZrO2+TaO2.5) of components, such as ZrO2 and TaO2.5, an increase in the content of which has the effect of greatly increasing the refractive index and slightly reducing the Abbé number; (4) the total quantity of high refractive index, high dispersion elements, such as TiO2, NbO2.5, WO3, and BiO1.5, an increase in the content of which has the effect of greatly increasing the refractive index and greatly reducing the Abbé number; (5) the total quantity of monovalent and divalent components, such as LiO0.5 and ZnO, an increase in the content of which has the effects of lowering the melting temperature of the glass starting materials, enhancing the stability of the glass, lowering the liquidus temperature, lowering the glass transition temperature, and the like; and (6) the total quantity of components other than those listed above. Among these, the adjustment of (1) to (4) above is effective for adjusting optical characteristics.
Specifically, the following applies for important components (1) to (3) of the present invention. The upper limit of (1) NWF is desirably 75 percent, preferably 72 percent, more preferably 70 percent, still more preferably 68 percent, still more preferably 66 percent, still more preferably 64 percent, and yet more preferably, 62 percent. Additionally, the lower limit of NWF is desirably 48 percent, preferably 50 percent, more preferably 52 percent, still more preferably 53 percent, still more preferably 54 percent, still more preferably 55 percent, and yet more preferably, 56 percent. The upper limit of (2) ΣRE is desirably 35 percent, preferably 34 percent, more preferably 33 percent, still more preferably 32 percent, still more preferably 31 percent, still more preferably 30 percent, and yet more preferably, 29 percent. Additionally, the lower limit of ΣRE is desirably 14 percent, preferably 16 percent, more preferably 17 percent, still more preferably 18 percent, still more preferably 20 percent, still more preferably 22 percent, still more preferably 23 percent, and yet more preferably, 24 percent. The upper limit of (3) (ZrO2+TaO2.5) is desirably 5 percent, preferably 4 percent, more preferably 3.5 percent, still more preferably 3 percent, still more preferably 2.5 percent, still more preferably 2 percent, still more preferably 1.5 percent, still more preferably 1 percent, and yet more preferably, 0.5 percent. Optimally, (ZrO2+TaO2.5) constitutes 0 percent.
The quantities of ΣRE and NWF can be adjusted by referencing the ratio of ΣRE and NWF, namely, ΣRE/NWF. The upper limit of ΣRE/NWF is desirably 0.8, preferably 0.75, more preferably 0.70, still more preferably 0.65, still more preferably 0.60, still more preferably 0.55, and yet more preferably, 0.50. Additionally, the lower limit of ΣRE/NWF is desirably 0.15, preferably 0.20, more preferably 0.25, still more preferably 0.30, still more preferably 0.35, still more preferably 0.40, and yet more preferably, 0.45.
Additional conditions are as follows. To lower the liquidus temperature by mixing rare earth components, thereby raising (maintaining) the stability of a glass with relatively good optical characteristics, it is desirable to pay attention to the ratio of LaO1.5 to the total quantity of rare earth elements ΣRE, namely LaO1.5/ΣRE. In Form C, which permits a total quantity of ΣRE that is smaller than that in Form A by limiting the quantities of Zr and Ta incorporated as set forth above, LaO1.5/ΣRE assumes a wide range of values. That is, the upper limit of LaO1.5/ΣRE is desirably 0.9, preferably 0.80, more preferably 0.70, still more preferably 0.60, still more preferably 0.57, and yet more preferably, 0.55. Additionally, the lower limit of LaO1.5/ΣRE is desirably 0.30, preferably 0.4, more preferably 0.45, and yet more preferably, 0.48. In glasses in which the total amount of ΣRE is 20 or lower, LaO1.5/ΣRE can be kept to 0.80 or higher.
In particular, in Form C, in addition to essential rare earth components, it is desirable to achieve a lower refractive index and lower dispersion than in Form A by not incorporating large amounts of the high refractive index and high dispersion components of Zr, Ta, Ti, Nb, W, and Bi. Limiting the quantities of Ta and Zr that are incorporated in Form C is extremely effective for enhancing the optical characteristics and molding properties of the glass.
TiO2 and NbO2.5 can be further incorporated into Form C as optional components. TiO2 and NbO2.5 function to increase the refractive index while maintaining low dispersion. However, since they also increase dispersion, TiO2 is set to 0 to 2 percent and NbO2.5 to 0 to 3 percent.
Other high refractive index and high dispersion components can be incorporated to the extent that the effect of the present invention is not spoiled. The upper limit of the total quantity (TiO2+NbO2.5+WO3+BiO1.5) of high refractive index and high dispersion components such as TiO2, NbO2.5, WO3, and BiO1.5 is desirably 4 percent, preferably 3 percent, still more preferably 2 percent, and yet more preferably, 1 percent. Optimally, none of these components is incorporated at all.
(ZnO+3ZrO2+5TaO2.5) is set to 15 percent or less to maintain low dispersion.
(2LiO0.5+ZnO+(F/2)) is set to 25 percent or more because the ratio of NWF in Form C is greater than in Form A and the glass transition point (Tg) tends to be high. The increase in the quantity of these Tg-lowering components yields a lower glass transition temperature.
To achieve lower dispersion in Form C than in Forms A, B, and D, the ratio of NWF to ΣRE is greater, and a large quantity of BO1.5 is incorporated. Thus, the upper limit of BB—(BO—BB) of +60 is a greater value than in Forms A, B, and D. As a result, by keeping F/O, which denotes the content of F, an element contributing to volatilization, to 0.21 or lower, it is possible to compensate for the reduction in the volatilization-inhibiting effect due to a high upper limit of BB—(BO—BB).
In the optical glass of Form C, the refractive index nd and the Abbé number νd desirably satisfy equation (3) below. The relation between the refractive index nd and the Abbé number νd is described further below.

nd−(2.25−0.01×νd)≧−0.01  (3)

Form D is a glass suited to realizing optical constants in the form of a refractive index nd of 1.825 to 1.90 and an Abbé number νd of 35 to 43.
The facts that Form D is an optical glass comprising, denoted as cationic percentages:

















BO1.5 
20 to 70
percent;



LaO1.5
6 to 30
percent;



GdO1.5
4 to 25
percent;










as well as O and F, and that the F/O molar ratio of the F content to the O content is 0.01 to 0.30, are shared with the optical glass of the first basic form of the present invention. A description of these compositions will be given further below with reference to Tables 1 and 2. Satisfying these conditions yields an optical glass with high refractive index and low dispersion characteristics, good thermal stability, and a low glass transition temperature, that is suited to precision press molding.

The fact that Form D is an optical glass comprising glass components in the form of cations including B and anions including 0 and F, such that the value of BB—(BO—BB) falls within a range of −60 to +60, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO, is shared with the optical glass of the second basic form of the present invention. Satisfying these conditions yields a quality optical glass containing glass components in the form of B, O, and F, that undergoes little volatilization in a melted state and exhibits little variation in various characteristics such as optical characteristics. However, in Form D the upper limit of BB—(BO—BB) is 0. The reason for this is as follows. To raise the refractive index of Form D higher than in Forms A, B, and C, large quantities of components with high melting points, such as rare earth elements, Zr, and Ta, are included among the glass components. This increases the liquidus temperature, making it necessary to reduce NWF components that lower the refractive index. Thus, the liquidus temperature increases, and the temperature at which the glass flows out tends to rise. Accordingly, to inhibit the volatilization of glass components at this higher temperature, the value of the upper limit, indicating the ratio of volatilizable bonding in the glass system, is strictly limited.
The fact of comprising

















SiO2
0 to 20
percent;



ZrO2
0 to 8
percent;



TaO2.5
0 to 10
percent;



TiO2
0 to 8
percent;



NbO2.5
0 to 8
percent;



WO3
0 to 10
percent; and



GeO2
0 to 5
percent










is also shared with the optical glasses of the first and second basic forms of the present invention. The compositions thereof will be described further below with reference to Tables 1 and 2.

The quantity of ZrO2 is set to 8 percent or less because when the content of ZrO2 exceeds 8 percent, dispersion and the liquidus temperature tend to increase. The upper limit of the ZrO2 content is desirably 6 percent, preferably 5 percent, more preferably 4 percent, still more preferably 3.5 percent, and yet more preferably, 3 percent. The lower limit of the ZrO2 content is desirably 0 percent, preferably 0.5 percent, more preferably 1 percent, still more preferably 1.5 percent, and yet more preferably, 2 percent.
The content of TaO2.5 is limited to 10 percent or less because when the content of TaO2.5 exceeds 10 percent, it becomes difficult to maintain the desired dispersion and good stability. The upper limit of the TaO2.5 content is desirably 9 percent, preferably 8 percent, more preferably 7 percent, and still more preferably, 6 percent. The lower limit of the TaO2.5 content is desirably 1 percent, preferably 2 percent, more preferably 3 percent, still more preferably 4 percent, and yet more preferably, 4.5 percent.
In particular, as set forth above, since Form D is an optical glass having optical constants in the form of a refractive index nd of 1.825 to 1.90 and an Abbé number νd of 35 to 43, to achieve an optical glass achieving both this refractive index nd and Abbé number νd, it suffices to classify the glass components as follows in the same manner as in Form A and adjust their contents. That is, it suffices to adjust: (1) the total quantity NWF of glass forming components, such as BO1.5, SiO2, and AlO1.5, an increase in the content of which has the effect of reducing the refractive index and increasing the Abbé number; (2) the total quantity ΣRE of rare earth components, such as LaO1.5, GdO1.5, and YO1.5, an increase in the content of which has the effect of increasing the refractive index and slightly reducing the Abbé number, thereby increasing the refractive index and lowering the dispersion of the glass; (3) the total quantity (ZrO2+TaO2.5) of components, such as ZrO2 and TaO2.5, an increase in the content of which has the effect of greatly increasing the refractive index and slightly reducing the Abbé number; (4) the total quantity of high refractive index, high dispersion elements, such as TiO2, NbO2.5, WO3, and BiO1.5, an increase in the content of which has the effect of greatly increasing the refractive index and greatly reducing the Abbé number; (5) the total quantity of monovalent and divalent components, such as LiO0.5 and ZnO, an increase in the content of which has the effects of lowering the melting temperature of the glass starting materials, enhancing the stability of the glass, lowering the liquidus temperature, lowering the glass transition temperature, and the like; and (6) the total quantity of components other than those listed above. Among these, the adjustment of (1) to (4) above is effective for adjusting optical characteristics.
Specifically, the following applies for important components (1) to (3) of the present invention. The upper limit of (1) NWF is desirably 49 percent, preferably 46 percent, more preferably 44 percent, still more preferably 43 percent, still more preferably 42 percent, still more preferably 41 percent, and yet more preferably, 40 percent. Additionally, the lower limit of NWF is desirably 32 percent, preferably 33 percent, more preferably 34 percent, still more preferably 35 percent, still more preferably 36 percent, and yet more preferably, 37 percent. The upper limit of (2) ΣRE is desirably 36 percent, preferably 35 percent, more preferably 34 percent, still more preferably 33 percent, still more preferably 32 percent, still more preferably 31 percent, and yet more preferably, 30 percent. Additionally, the lower limit of ΣRE is desirably 21 percent, preferably 22 percent, more preferably 23 percent, still more preferably 24 percent, still more preferably 25 percent, and yet more preferably, 26 percent. The upper limit of (3) (ZrO2+TaO2.5) is desirably 12 percent, preferably 11 percent, more preferably 10 percent, still more preferably 9.5 percent, still more preferably 9 percent, still more preferably 8.5 percent, and yet more preferably, 8 percent. Additionally, the lower limit of (ZrO2+TaO2.5) is desirably 3 percent, preferably 4 percent, more preferably 5 percent, still more preferably 5.5 percent, still more preferably 6 percent, still more preferably 6.5 percent, and yet more preferably, 7 percent.
The quantities of ΣRE and NWF can be adjusted by referencing the ratio of ΣRE and NWF, namely, ΣRE/NWF. The upper limit of ΣRE/NWF is desirably 1.2, preferably 1.1, more preferably 1.0, still more preferably 0.95, still more preferably 0.9, still more preferably 0.85, and yet more preferably, 0.8. Additionally, the lower limit of ΣRE/NWF is desirably 0.45, preferably 0.50, more preferably 0.55, still more preferably 0.60, still more preferably 0.65, and yet more preferably, 0.70.
Additional conditions are as follows. To lower the liquidus temperature by mixing rare earth components, thereby raising (maintaining) the stability of a glass with relatively good optical characteristics, it is desirable to pay attention to the ratio of LaO1.5 to the total quantity of rare earth elements ΣRE, namely LaO1.5/ΣRE. In Form D, which has the above-described desirable component structure into which suitable quantities of Zr and Ta have been introduced in this manner, a ratio in which a large amount of La is employed is effective. That is, the upper limit of LaO1.5/ΣRE is desirably 0.9, preferably 0.85, more preferably 0.8, still more preferably 0.77, and yet more preferably, 0.75. Additionally, the lower limit of LaO1.5/ΣRE is desirably 0.5, preferably 0.55, still more preferably 0.60, still more preferably 0.65, and yet more preferably, 0.70.
In particular, in Form D, in addition to essential rare earth components, it is desirable to preferentially incorporate Zr and Ta from among the high refractive index and high dispersion elements of Zr, Ta, Ti, Nb, W, and Bi. It is also desirable to incorporate optimal quantities of Ti, Nb, W, and Bi to achieve a higher refractive index and greater dispersion than in Forms A, B, and C. Further, in addition to the quantities of Ta and Zr incorporated in Form D, based on the optical characteristics being sought, the incorporation of certain quantities of Ti, Nb, W, and Bi is extremely effective for enhancing the optical characteristics and molding properties of the glass.
The incorporation of WO3 into Form D as an optional component is particularly effective to raise the refractive index and lower the liquidus temperature. The upper limit of WO3 is desirably 10 percent, preferably 8 percent, more preferably 7 percent, still more preferably 6 percent, and yet more preferably, 5.5 percent. The lower limit is desirably 0 percent, preferably 1 percent, more preferably 2 percent, still more preferably 3 percent, and yet more preferably, 4 percent. The incorporation of 3 percent or more of WO3, preferably 4 percent or more, is desirable when raising nd to 1.87 or higher.
TiO2 and NbO2.5 can be further incorporated into Form D as optional components. TiO2 and NbO2.5 function to increase the refractive index while maintaining low dispersion. However, since they also increase dispersion, TiO2 is set to 0 to 5 percent and NbO2.5 to 0 to 5 percent.
Other high refractive index and high dispersion components can be incorporated to the extent that the effect of the present invention is not spoiled. The upper limit of the total quantity (TiO2+NbO2.5+WO3+BiO1.5) of high refractive index and high dispersion components such as TiO2, NbO2.5, WO3, and BiO1.5 is desirably 12 percent, preferably 11 percent, more preferably 10 percent, still more preferably 9 percent, still more preferably 8 percent, still more preferably 7 percent, and yet more preferably, 6 percent. From the perspectives of maintaining the stability of the glass and raising the refractive index without markedly increasing the liquidus temperature, the lower limit of the total quantity (TiO2+NbO2.5+WO3+BiO1.5) of high refractive index and high dispersion components is desirably 1 percent, preferably 2 percent, more preferably 3 percent, still more preferably 4 percent, and yet more preferably, 5 percent.
The fact of comprising:

















LiO0.5
0 to 10
percent;



ZnO
0 to 28
percent; and



YbO1.5
0 to 3
percent










differs from the optical glasses of the first and second basic forms of the present invention.

LiO0.5 is set to 0 to 10 percent because when the content of LiO0.5 exceeds 10 percent, the refractive index tends to decrease, the liquidus temperature rises, and the viscosity of the glass melt tends to decrease. Thus, the LiO0.5 content is set to 10 percent or lower. The upper limit of the LiO0.5 content is desirably 7 percent, preferably 5 percent, and more preferably, 4.5 percent. The lower limit of the LiO0.5 content is desirably 1 percent, preferably 2 percent, and more preferably, 2.5 percent.
ZnO is set to 0 to 28 percent because, in terms of optical characteristics, the refractive index increases somewhat and there is a problem in the form of increased dispersion (a reduction in νd) when a large quantity of ZnO is incorporated. In Form D, the object is to obtain a glass having a higher refractive index of nd=1.825 to 1.90 and a higher dispersion range of νd=35 to 43 than in Forms A, B, and C. Thus, the content permitted has been increased relative to what it is in the glasses of Forms A, B, and C. Thus, 2LiO0.5/(2LiO0.5+ZnO), which serves as a yardstick for adjusting components that lower the Tg, naturally assumes a lower value. That is, the upper limit of 2LiO0.5/(2LiO0.5+ZnO) is desirably 0.7, preferably 0.6, more preferably 0.5, and still more preferably, 0.4. The lower limit of 2LiO0.5/(2LiO0.5+ZnO) is desirably 0, preferably 0.05, more preferably, 0.1, still more preferably 0.15, still more preferably 0.2, and yet more preferably, 0.25.
YbO1.5 is set to 0 to 3 percent because of the high cost of YbO1.5 and because the incorporation of an excessive quantity increases the liquidus temperature, indirectly fostering the volatilization of glass components and compromising the homogeneity and molding characteristics of the glass. Further, this component absorbs radiation in the infrared region, rendering the glass unsuitable for use in highly sensitive optical systems of which sensitivity characteristics in the near infrared range are required, such as high-precision video cameras and surveillance cameras. However, the glass of Form D has a high refractive index, so its use can be effectively limited to applications such as compact digital cameras that do not receive light in the infrared range. YbO1.5 can be incorporated with 3 percent as the upper limit. The upper limit is set at 3 percent for YbO1.5 because of its high cost and the fact that it absorbs infrared radiation.
(2LiO0.5+ZnO+(F/2)) is set to 20 percent or more to lower the glass transition temperature.
Further, in the optical glass of Form D, the refractive index nd and the Abbé number νd desirably satisfy equation (4). The relation between the refractive index nd and the Abbé number νd is described further below.

nd−(2.25−0.01×νd)≧−0.01  (4)

The actions and effects of individual glass components will be described sequentially below. Tables 1-1 to 1-29 and 2-1 to 2-18 give the values of desirable upper limit and lower limit values for the ranges of physical properties and components. For both the upper limit and lower limit, the value indicated as number 1 is the outermost value of the numeric range. As the number indicated increases to 2, 3, 4, 5, 6, 7, or 8, the upper limit and the lower limit lie further inside the numeric range and increase in desirability. In the upper limit and lower limit fields of each table, the value indicated by the largest number is the most desirable value (upper limit value or lower limit value). The upper limit value and lower limit value of Tables 1-1 to 1-29 and 2-1 to 2-18 can be combined.
BO1.5 is an essential component in the optical glass of the present invention that forms a glass network. Incorporating BO1.5 into the optical glass of the present invention in a range of from 20 to 70 percent has the effect of enhancing glass stability. Incorporating 20 percent or more of BO1.5 has the effects of enhancing low dispersion and lowering the liquidus temperature. It is undesirable for the content of BO1.5 to exceed 70 percent because the refractive index decreases and the amount of volatilization tends to increase. From these perspectives, in the basic forms and in Forms A, B, C, and D of the present invention, the upper and lower limits of the BO1.5 content are suitably set as indicated below. In particular, from the perspective of increasing the refractive index, the upper limit in Form D is set to a lower value than in the basic forms. The lower limit in Form C is set to a higher value than in the basic forms to increase νd.







TABLE 1-1







BO1.5 (Cation %)














Form
Basic
A
B
C
D


















Upper limit
1
70
65
64
69
45




2
65
60
57
65
43




3
60
51
52
60
42




4
55
48
48
55
41




5
51
46
45
53
40




6
48
44
43
51
39




7
46
42
41
50
38




8
44

39






9
42







Lower limit
1
20
25

40
24




2
30
28
24
42
26




3
34
30
28
44
28




4
36
34
31
46
29




5
38
36
33

30




6
39
38
34






7
40
39
35






8

40









SiO2 is an optional component in the optical glass of the present invention that forms a glass network. SiO2 can be incorporated into the optical glass of the present invention within a range of 0 to 20 percent. This has the effect of markedly improving glass stability. Incorporating more than 0 percent of SiO2 has the effects of increasing the melt viscosity, lowering the liquidus temperature, and enhancing mechanical strength. An SiO2 content exceeding 20 percent is undesirable in that the refractive index tends to decrease and the glass transition temperature tends to rise. From these perspectives, the upper and lower limits of the SiO2 content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention.







TABLE 1-2







SiO2 (Cation %)














Form
Basic
A
B
C
D


















Upper limit
1
20
17
16
17
15




2
17
15
13
15
10




3
15
13
11
13
8




4
13
12
10
12
7




5
12
11
9
11
6




6
11



5



Lower limit
1
0
2
0
2
1




2
2
4
2
4
2




3
5
5
4
5
3




4
7
7
5
7





5
8
8
6
8





6
9
9
7
9





7
10

8









The desirable range of the combined quantities of BO1.5 and SiO2 is given below.

    Basic forms: 32 to 74 percent, preferably 36 to 70 percent.
    Form A: 42 to 61 percent, 44 to 59 percent, 46 to 57 percent, 48 to 55 percent (increasing in desirability from left to right; identical below);
    Form B: 39 to 57 percent, 41 to 55 percent, 43 to 53 percent, 45 to 51 percent;
    Form C: 50 to 72 percent, 52 to 70 percent, 54 to 68 percent, 56 to 66 percent;
    Form D: 30 to 46 percent, 32 to 45 percent, 34 to 44 percent, 35 to 43 percent.


AlO1.5 and GeO2 are components that function to form a glass network in a manner equivalent to BO1.5 and SiO2. When these components are incorporated into the optical glass of the present invention, the above total content ranges apply to AlO1.5 and GeO2 as well as to BO1.5 and SiO2. However, the effect of AlO1.5 is inferior to that of BO1.5 and SiO2. Thus, the incorporation of BO1.5 and SiO2 is preferred to the incorporation of AlO1.5. Since GeO2 is expensive, the incorporation of BO1.5 and SiO2 is preferable to the incorporation of GeO2.
LaO1.5 is an essential component of the optical glass of the present invention that raises the refractive index. Incorporating LaO1.5 within a range of 6 to 30 percent in the optical glass of the present invention has the effect of raising the refractive index. The incorporation of 6 percent or more of LaO1.5 has the effects of maintaining low dispersion, enhancing chemical durability, and increasing mechanical strength. LaO1.5 has a lower melting point than other rare earth components, and is advantageous in that it can be incorporated in large quantity. The incorporation of more than 30 percent of LaO1.5 is undesirable in that the glass stability decreases, the liquidus temperature rises, and the glass transition temperature rises. From these perspectives, the upper and lower limits of the LaO1.5 content are suitably set as indicated below for the basic forms and forms A, B, C, and D of the present invention. In particular, from the perspective of raising the refractive index, the lower limit in Form D is set higher than in the basic forms.







TABLE 1-3







LaO1.5 (Cation %)














Form
Basic
A
B
C
D


















Upper limit
1
30
25

24
27




2
25
22
26
22
26




3
22
20
24
20
24




4
20
18
23
18
22




5
18
17
22
17





6
17
16
21
16





7
16







Lower limit
1
6
8
8
6
14




2
8
9
11
8
16




3
9
10
14
9
17




4
10
11
16
10
18




5
11
12
18
11





6
12

19
12









GdO1.5 is an essential component of the optical glass of the present invention that raises the refractive index. Incorporating GdO1.5 into the optical glass of the present invention within a range of 4 to 25 percent has the effect of raising the refractive index. The incorporation of 4 percent or more of GdO1.5 has the effects of maintaining low dispersion, enhancing chemical durability, and increasing mechanical strength. GdO1.5 affords an advantage in that it lowers the melting point and increases moldability when mixed with other rare earth components. The incorporation of a quantity of GdO1.5 exceeding 25 percent is undesirable in that it decreases glass stability, raises the liquidus temperature, and raises the glass transition temperature. From such perspectives, the upper and lower limits of the GdO1.5 content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. In particular, the upper limit in Form D is set to a lower value than in the basic forms from the perspective of setting a desirable LaO1.5/ΣRE ratio that does not raise the liquidus temperature when high dispersion components are incorporated.







TABLE 1-4







GdO1.5 (Cation %)














Form
Basic
A
B
C
D


















Upper limit
1
25
22
22
20
18




2
22
20
20
18
16




3
20
18
18
16
14




4
18
16
16
15
12




5
16
15
15
14
11




6
15
14
14

10




7
14







Lower limit
1
4
6
6
6
5




2
6
7
7
7
5.5




3
7
8
8
8
6




4
8
9
9
9
6.5




5
9
10
10
10





6
10









YO1.5 is an optional component in the optical glass of the present invention that raises the refractive index. The optical glass of the present invention can contain YO1.5 within a range of 0 to 10 percent, which has the effect of raising the refractive index. the incorporation of more than 0 percent of YO1.5 has the effects of maintaining low dispersion, enhancing chemical durability, and increasing mechanical strength. Further, YO1.5 affords an advantage in that it lowers the melting point and increases moldability when mixed with other rare earth components. Still further, YO1.5 has a high refractive index for its specific gravity, contributing to the reduction in weight of lenses comprised of the optical glass of the present invention. The incorporation of a quantity of YO1.5 exceeding 10 percent is undesirable because it decreases glass stability, raises the liquidus temperature, and raises the glass transition temperature. From such perspectives, the upper and lower limits of the YO1.5 content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. In particular, the upper limit in Form D is set to a lower value than in the basic forms from the perspectives of setting a desirable LaO1.5/ΣRE ratio that does not raise the liquidus temperature when high dispersion components are incorporated, and of preferentially employing rare earth components with high refractive indexes.







TABLE 1-5







YO1.5 (Cation %)














Form
Basic
A
B
C
D


















Upper limit
1
10
7
7
7
5




2
7
5
5
5
3




3
5
4
4
4
2




4
4
3
3
3
1




5
3

2
2.5
0




6



2





7



1.5





8



1





9



0.5





10



0




Lower limit
1
0
0
0






2
0.5
0.5
0.5






3
1
1
1






4
1.5
1.5







5
2
2







6
2.5
2.5









LiO0.5 is an optional component of the optical glass of the present invention that lowers the glass transition temperature, sag temperature, and press molding temperature. LiO0.5 can be incorporated into the optical glass of the present invention in a range of from 0 to 20 percent, having the effect of markedly lowering the glass transition temperature. The incorporation of more than 0 percent of LiO0.5 yields a glass of higher density than other alkalis. As a result, it is possible to achieve an optical glass of higher refractive index than with other alkalis. The incorporation of more than 20 percent of LiO0.5 lowers the melt viscosity, raises the liquidus temperature, and as a result, decreases glass stability. Further, the incorporation of more than 20 percent of LiO0.5 is undesirable in that it lowers the refractive index. From such perspectives, the upper and lower limits of the LiO0.5 contents are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. The upper limit of Form D is set to a value that is lower than those of the basic forms because high dispersion is permitted and Li and Zn are employed as components that lower the Tg.







TABLE 1-6







LiO0.5 (Cation %)














Form
Basic
A
B
C
D


















Upper limit
1
20
16
16
18
8




2
16
13
13
16
7




3
13
12
10
14
6




4
12
11
7
13
5




5
11
10
5
12





6
10

4






7








Lower limit
1
0
2
0
2
0




2
2
4
0.5
4
1




3
4
5
1
5
2




4
5
6
1.5
6
3




5
6
7
2
7





6
7
8
2.5
8





7
8

3
10









ZnO is an optional component in the optical glass of the present invention that lowers the glass transition temperature, sag temperature, and press molding temperature. The optical glass of the present invention can comprise ZnO within a range of 0 to 20 percent, thereby lowering the glass transition temperature. The incorporation of more than 0 percent of ZnO raises the refractive index, lowers the liquidus temperature, and suppresses volatilization more than Tg lowering components. The incorporation of more than 20 percent of ZnO is undesirable in that it increases dispersion (reduces νd) and lowers the nd relative to the specific gravity. From such perspectives, the upper and lower limits of the ZnO content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. From the perspective of increasing a low level of dispersion, the upper limit of Form C is set to a lower value than the basic forms. From the perspective of raising the refractive index, the lower limit of Form D is set to a value that is higher than that of the basic forms.







TABLE 1-7







ZnO (Cation %)














Form
Basic
A
B
C
D


















Upper limit
1
20
17
25
6
28




2
17
14
20
4
26




3
14
12
19
3
24




4
12
10
18
2
22




5
10
8
17
2
21




6
8
7
16

20




7
7

15






8


14





Lower limit
1
0
1
0
0
5




2
1
2
3
0.5
8




3
2
3
5
1
10




4
3
4
8

12




5
4
5
10

13




6
5

11

14




7


12

15









F is an essential component of the optical glass of the present invention that lowers the glass transition temperature, sag temperature, and press molding temperature. In the optical glass of the present invention, the molar ratio F/O of the F content to the O (oxygen) content is 0.01 to 0.30. Incorporating F within this range has the effect of lowering the glass transition temperature. Incorporating F in a quantity such that F/O is 0.01 or greater permits an increase in the quantity of rare earth components incorporated, enhances glass stability, and improves weatherability. The incorporation of F in a quantity such that F/O exceeds 0.30 is undesirable in that it promotes variation in characteristics due to volatilization, increases striae, lowers the refractive index, lowers the melt viscosity, and markedly diminishes the nd relative to the specific gravity. From such perspectives, the upper and lower limits of the F content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention.







TABLE 1-8







F/O (Molar ratio)














Form
Basic
A
B
C
D
















Upper limit
1
0.30
0.24
0.27
0.24
0.20



2
0.27
0.21
0.24
0.21
0.16



3
0.24
0.18
0.22
0.18
0.14



4
0.21
0.16
0.20
0.16
0.12



5
0.18
0.14
0.18
0.14
0.10



6
0.16
0.12
0.17
0.12
0.08



7
0.14
0.11
0.16
0.11
0.07



8
0.12

0.15





9
0.11






Lower limit
1
0.01
0.01
0.01
0.01
0.01



2
0.02
0.02
0.03
0.02
0.02



3
0.04
0.04
0.06
0.04
0.04



4
0.06
0.06
0.08
0.06




5
0.08
0.08
0.09
0.08




6
0.09
0.09
0.10
0.09









ZrO2 is an optional component of the optical glass of the present invention that raises the refractive index. ZrO2 can be incorporated in a quantity falling within a range of 0 to 8 percent in the optical glass of the present invention, having the effect of markedly raising the refractive index. The incorporation of a quantity of ZrO2 of greater than zero percent has the effects of stabilizing the glass, lowering the liquidus temperature more than rare earth components, raising the viscosity, enhancing chemical durability, and increasing mechanical strength. The incorporation of a quantity of ZrO2 exceeding 8 percent is undesirable in that it somewhat increases dispersion (reduces νd) and raises the glass transition temperature. From such perspectives, the upper and lower limits of ZrO2 are suitably set as indicated below in the basic forms and Forms A, B, C, and D of the present invention. From the perspective of increasing νd, the upper limits of Forms A and C are set to lower values than in the basic forms.







TABLE 1-9







ZrO2 (Cation %)














Form
Basic
A
B
C
D


















Upper limit
1
8
3.8

5.0
6.0




2
5
3.4
5
4.0
5.0




3
4.5
3.0
4.5
3.0
4.0




4
3.8
2.7
3.8
2.5
3.5




5
3.4
2.5
3.4
2.0
3.0




6
3

3
1.5





7
2.7

2.7
1.0





8
2.5

2.5
0.5




Lower limit
1
0
0
0

0




2
0.5
0.5
0.5

0.5




3
1
1
1

1




4
1.5
1.5
1.5

1.5




5
2
2
2

2









TaO2.5 is an optional component of the optical glass of the present invention that raises the refractive index. TaO2.5 can be incorporated into the optical glass of the present invention within a range of 0 to 10 percent, having the effect of markedly raising the refractive index. Incorporating a quantity of TaO2.5 of greater than zero percent has the effects of stabilizing the glass more than rare earth components, lowering the liquidus temperature more than rare earth components, raising the viscosity, enhancing chemical durability, and increasing mechanical strength. The incorporation of a quantity of TaO2.5 exceeding 10 percent is undesirable in that it increases dispersion (lowers νd) somewhat and increases the cost of the glass. From such perspectives, the upper and lower limits of the TaO2.5 content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. In particular, from the perspective of lowering dispersion, the upper limits of Forms A and C are set to lower values than for the basic forms.







TABLE 1-10







TaO2.5 (Cation %)














Form
Basic
A
B
C
D


















Upper limit
1
10
5
10
3
10




2
7
4
8
2
9




3
5
3
7
1
8




4
4
2
6
0.5
7




5
3
1.5
5.5
0
6




6
2
1.2
4.8






7
1.5

4.3






8
1.2

4





Lower limit
1
0
0
0

0




2
0.1
0.1
0.5

1




3
0.3
0.3
1.2

2




4
0.5
0.5
1.8

3




5
0.6
0.6
2.3

4




6


2.7

5




7


3









WO3 is an optional component of the optical glass of the present invention that raises the refractive index. WO3 can be incorporated into the optical glass of the present invention within a range of 0 to 10 percent, having the effect of markedly raising the refractive index. Incorporating a quantity of WO3 of greater than zero percent has the effects of stabilizing the glass more than rare earth components, lowering the liquidus temperature more than rare earth components, and raising the viscosity somewhat. The incorporation of a quantity of WO3 exceeding 10 percent is undesirable in that it markedly increases dispersion (lowers νd). From such a perspective, the upper and lower limits of the WO3 content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. In particular, from the perspective of lowering dispersion, the upper limit of Form C is set to a lower value than for the basic forms. From the perspective of raising the refractive index, the lower limit of Form D is set to a higher value than for the basic Forms.







TABLE 1-11







WO3 (Cation %)














Form
Basic
A
B
C
D


















Upper limit
1
10
5
5
2
10




2
8
3
3
1
8




3
5
2
2
0.5
7




4
3
1
1
0
6




5
2
0
0

5.5




6
1








7
0







Lower limit
1
0



0




2




1




3




2




4




3




5




4









NbO2.5 is an optional component of the optical glass of the present invention that raises the refractive index. NbO2.5 can be incorporated into the optical glass of the present invention within a range of 0 to 8 percent, having the effect of markedly raising the refractive index. Incorporating a quantity of NbO2.5 of greater than zero percent has the effects of stabilizing the glass more than rare earth components, lowering the liquidus temperature more than rare earth components, and raising the viscosity somewhat. The incorporation of a quantity of NbO2.5 exceeding 8 percent is undesirable in that it markedly increases dispersion (lowers νd). From such a perspective, the upper and lower limits of the NbO2.5 content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. In particular, from the perspectives of lowering dispersion and the liquidus temperature, the upper limits of Forms A, B, and C are set to a lower value than for the basic forms.







TABLE 1-12







NbO2.5 (Cation %)














Form
Basic
A
B
C
D


















Upper limit
1
8
3
2
2
5




2
5
2
1
1
3




3
3
1
0
0.5
2




4
2
0

0
1




5
1



0




6
0
















Lower limit 1
0



0









TiO2 is an optional component of the optical glass of the present invention that raises the refractive index. TiO2 can be incorporated into the optical glass of the present invention within a range of 0 to 8 percent, having the effect of markedly raising the refractive index. Incorporating a quantity of TiO2 of greater than zero percent has the effects of stabilizing the glass more than rare earth components, lowering the liquidus temperature more than rare earth components, and raising the viscosity somewhat. The incorporation of a quantity of TiO2 exceeding 8 percent is undesirable in that it markedly increases dispersion (lowers νd). From such a perspective, the upper and lower limits of the TiO2 content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. In particular, from the perspective of lowering dispersion, the upper limits of Forms A, B, and C are set to a lower value than for the basic forms.







TABLE 1-13







TiO2 (Cation %)














Form
Basic
A
B
C
D


















Upper limit
1
8
3
5
2
5




2
5
2
3
1
3




3
3
1
2
0.5
2




4
2
0
1
0
1




5
1

0

0




6
0
















Lower limit 1
0













AlO1.5 is an optional component of the optical glass of the present invention that forms a glass network. AlO1.5 can be incorporated into the optical glass of the present invention within a range of 0 to 10 percent, having the effect of somewhat enhancing glass stability. Incorporating a quantity of AlO1.5 of greater than zero percent has the effects of lowering dispersion, somewhat raising viscosity, enhancing chemical durability, and increasing mechanical strength. The incorporation of a quantity of AlO1.5 exceeding 10 percent is undesirable in that it lowers the refractive index and tends to raise the glass transition temperature and liquidus temperature. From such perspectives, the upper and lower limits of the AlO1.5 content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. In particular, from the perspective of raising the refractive index, the upper limit of Form D is set to a lower value than for the basic forms.







TABLE 1-14







AlO1.5 (Cation %)














Form
Basic
A
B
C
D



















Upper limit
1
10
3
5
10
3




2
7
2
3
7
2




3
5
1
2
5
1




4
3
0
1
3
0




5
2

0
2




6
1


1




7
0.5


0




8
0











Lower limit 1
0










GeO2 is an optional component of the optical glass of the present invention that forms a glass network. GeO2 can be incorporated into the optical glass of the present invention within a range of 0 to 5 percent, having the effect of somewhat increasing the stability of the glass. Incorporating a quantity of GeO2 of greater than zero percent has the effects of somewhat increasing viscosity and raising the refractive index more than SiO2. The incorporation of a quantity of GeO2 exceeding 5 percent is undesirable in that it raises the cost of the glass. From such perspectives, the upper and lower limits of the GeO2 content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. Although the use of GeO2 is advantageous in terms of characteristics, it is quite expensive. Thus, the quantity of GeO2 is desirably minimized to obtain an optical glass having desired characteristics.







TABLE 1-15







GeO2 (Cation %)














Form
Basic
A
B
C
D



















Upper limit
1
5
5
5
5
5




2
3
3
3
3
3




3
2
2
2
2
2




4
1
1
1
1
1




5
0
0
0
0
0











Lower limit 1
0










GaO1.5 is an undesirable component that forms a glass network and can be incorporated to the extent that characteristics are maintained. GaO1.5 can be incorporated in the optical glass of the present invention in a range of 0 to 5 percent, having the effect of somewhat enhancing glass stability. The incorporation of a quantity of GaO1.5 of greater than zero percent has the effects of somewhat increasing viscosity and raising the refractive index more than SiO2. The incorporation of a quantity of GaO1.5 exceeding 5 percent is undesirable in that it raises the cost of the glass. From such perspectives, the upper and lower limits of the GaO1.5 content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention.







TABLE 1-16







GaO1.5 (Cation %)














Form
Basic
A
B
C
D



















Upper limit
1
5
3
3
3
3




2
3
2
2
2
2




3
2
1
1
1
1




4
1
0
0
0
0




5
0











Lower limit 1
0










PO2.5 is an undesirable component that forms a glass network and can be incorporated to the extent that characteristics are maintained. PO2.5 can be incorporated in the optical glass of the present invention in a range of from 0 to 5 percent. The incorporation of PO2.5 in a quantity exceeding 5 percent is undesirable in that it compromises the stability of the glass. From such perspectives, the upper and lower limits of the PO2.5 content is suitably determined as indicated below for the basic forms and Forms A, B, C, and D of the present invention.







TABLE 1-17







PO2.5 (Cation %)














Form
Basic
A
B
C
D



















Upper limit
1
5
3
3
3
3




2
3
2
2
2
2




3
2
1
1
1
1




4
1
0
0
0
0




5
0











Lower limit 1
0










NaO0.5, KO0.5, RbO0.5, and CsO0.5 are modifying components that can be incorporated to the extent that characteristics are maintained. The optical glass of the present invention can contain a total quantity of NaO0.5, KO0.5, RbO0.5, and CsO0.5 falling within a range of 0 to 10 percent. A quantity exceeding 10 percent is undesirable in that the stability of the glass is lower than with LiO0.5, the refractive index of the glass is reduced more than by LiO0.5, and the glass transition temperature rises more than with LiO0.5. From such perspectives, the upper and lower limits of the total quantity of NaO0.5, KO0.5, RbO0.5, and CsO0.5 are suitably set as indicated below.







TABLE 1-18







(Cation %)














Form
Basic
A
B
C
D



















Upper limit
1
10
5
5
7
5




2
7
3
3
5
3




3
5
2
2
3
2




4
3
1
1
2
1




5
2
0
0
1
0




6
1


0




7
0











Lower limit 1
0










MgO, CaO, SrO, and BaO are modifying components that can be incorporated to the extent that characteristics are maintained. The optical glass of the present invention can contain a total quantity of MgO, CaO, SrO, and BaO falling within a range of 0 to 10 percent. A quantity exceeding 10 percent is undesirable in that the stability of the glass is lower than with ZnO, the refractive index of the glass is reduced more than by ZnO, the glass transition temperature rises more than with ZnO, and the liquidus temperature rises more than with ZnO. From such perspectives, the upper and lower limits of the total quantity of MgO, CaO, SrO, and BaO are suitably set as indicated below.







TABLE 1-19







(Cation %)














Form
Basic
A
B
C
D



















Upper limit
1
10
7
7
10
7




2
7
5
5
7
5




3
5
3
3
5
3




4
3
2
2
3
2




5
2
1
1
2
1




6
1
0
0
1
0




7
0


0











Lower limit 1
0










ScO1.5, InO1.5, and LuO1.5 are modifying components that can be incorporated to the extent that characteristics are maintained. The optical glass of the present invention can contain a total quantity of ScO1.5, InO1.5, and LuO1.5 falling within a range of 0 to 10 percent. A quantity exceeding 10 percent is undesirable in that the stability of the glass is lowered more than by LaO1.5 and GdO1.5, the liquidus temperature is raised more than by LaO1.5 and GdO1.5, and the refractive index of the glass is reduced more than by LaO1.5 and GdO1.5 From such perspectives, the upper and lower limits of the total quantity of ScO1.5, InO1.5, and LuO1.5 are suitably set as indicated below.







TABLE 1-20







(Cation %)














Form
Basic
A
B
C
D



















Upper limit
1
10
3
3
5
3




2
7
2
2
3
2




3
5
1
1
2
1




4
3
0
0
1
0




5
2


0




6
1




7
0











Lower limit 1
0










YbO1.5 is a modifying component the incorporation of which is to be avoided to the extent possible due to absorption in the infrared region. The optical glass of the present invention can contain 0 to 9 percent of YbO1.5. A YbO1.5 content in excess of 9 percent is undesirable in that the stability of the glass is lowered more than by LaO1.5 and GdO1.5, the liquidus temperature is raised more than by LaO1.5 and GdO1.5, the refractive index of the glass is lowered more than by LaO1.5 and GdO1.5, and there is absorption in the infrared region. From such perspectives, the upper and lower limits of the YbO1.5 content are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. In particular, from the above-mentioned perspectives of cost, liquidus temperature, and infrared absorption, the upper limit of Form A is set lower than in the basic forms.







TABLE 1-21







YbO1.5 (Cation %)














Form
Basic
A
B
C
D



















Upper limit
1
9
0.5
3
3
3




2
5
0.4
2
2
2




3
3
0.2
1
1
1




4
1
0.1
0.5
0.5
0.5




5
0.4
0.0
0.4
0.4
0.4




6
0.2

0.2
0.2
0.2




7
0.1

0.1
0.1
0.1




8
0

0.0
0.0
0.0



Lower limit
1
0


0.1




2



0.2




3



0.4










BO1.5×F/O is an indicator of suppression of variation in characteristics due to volatilization. BO1.5 is denoted as a cationic percentage and F/O is the molar ratio of F and O. BO1.5×F/O falls within a range of 0.05 to 10.00. Volatilization of the glass is suppressed by reducing boron and fluorine. Accordingly, boron and fluorine compounds, and components produced by the reaction of such compounds with oxygen and water in the atmosphere, are thought to be the volatile components. Qualitatively, the quantity of such volatile components is proportional to the product of the boron concentration in the glass and the fluorine concentration in the glass. The smaller this value is, the lower the potential amount of volatilization from the glass. From such perspectives, the upper and lower limits of BO1.5×F/O are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. Further, the value of BO1.5×F/O can be suitably adjusted by adjusting the quantities of each of the components of BO1.5, F, and O incorporated into the optical glass. In particular, from the perspective of low dispersion, the upper limit for Form C is set higher than for the basic forms, and from the perspective of a high refractive index, the upper limit for Form D is set lower than for the basic forms. From the perspective of a high refractive index, the lower limit in Form B is set higher than for the basic forms.
The following components can be added to adjust the quantity of bubbles in the glass.
CeO2 can be added within a range of 0 to 2 percent to the extent that the effect of the present invention is not spoiled. The quantity of CeO2 added is desirably 0 to 1 percent, preferably falling within a range of 0 to 0.5 percent, more preferably 0 to 0.3 percent, still more preferably 0 to 0.1 percent, and yet more preferably, none is incorporated at all.
SnO2 can be added within a range of 0 to 2 percent to the extent that the effect of the present invention is not spoiled. The quantity of SnO2 added is desirably 0 to 1 percent, preferably 0 to 0.5 percent, more preferably 0 to 0.3 percent, still more preferably 0 to 0.1 percent, and yet more preferably, none is incorporated at all.
SbO1.5 can be added within a range of 0 to 1 percent to the extent that the effect of the present invention is not spoiled. The quantity of SbO1.5 added is desirably 0 to 0.5 percent, preferably falling within a range of 0 to 0.1 percent, more preferably falling within a range of 0 to 0.08 percent, still more preferably falling within a range of 0 to 0.05 percent. When SbO1.5 is added, 0.01 to 0.02 percent is desirably incorporated.
To achieve the object of the present invention, the total quantity of BO1.5, SiO2, GeO2, AlO1.5, LiO0.5, NaO0.5, KO0.5, MgO, CaO, SrO, BaO, ZnO, LaO1.5, GdO1.5, YO1.5, TiO2, ZrO2, TaO2.5, NbO2.5, WO3, YbO1.5, CeO2, SnO2, and SbO1.5 is desirably 95 percent or greater, preferably 96 percent or greater, more preferably 97 percent or greater, still more preferably 98 percent or greater, still more preferably 99 percent or greater, and still more preferably 99.5 percent or greater, with 100 percent being optimal.
To achieve the object of the present invention, the total quantity of BO1.5, SiO2, GeO2, AlO1.5, LiO0.5, NaO0.5, KO0.5, MgO, CaO, SrO, BaO, ZnO, LaO1.5, GdO1.5, YO1.5, TiO2, ZrO2, TaO2.5, NbO2.5, WO3, YbO1.5, CeO2, SnO2, SbO1.5 GaO1.5, PO2.5, ScO1.5, InO1.5, and LuO1.5 is desirably 98 percent or greater, preferably 99 percent or greater, more preferably 99.5 percent or greater, still more preferably 99.8 percent or greater, and still more preferably 99.9 percent or greater, with 100 percent being optimal.







TABLE 1-22







BO1.5 × F/O














Form
Basic
A
B
C
D



















Upper limit
1
10.00
8
10
15
5.0




2
8.00
6
9
12
4.5




3
6.00
5
8
10
4.0




4
5.00
4.75
7.5
8
3.5




5
4.75
4.5
7.25
6
3.0




6
4.50
4.25
7
5
2.5




7
4.25
4
6.75

2.0




8
4.00

6.5



Lower limit
1
0.50
0.5
0.5
2
0




2
1.00
1
2
2.5
0.5




3
2.00
2
3.5
3
1.0




4
2.50
2.5
4.5
3.5
1.5




5
3.00

5
4




6


5.5




7


6










Excess B—O—B bonds: D (=BB—(B0—BB)) is an indicator of the suppression of variation in characteristics due to volatilization, and falls within a range of −60 to +60. Among glass components, the volatilization of boron in particular affects the glass composition. The initial reaction marking the start of volatilization is thought to consist of the recombination of boron-oxygen bonds in the glass by fluorine ions. At that time, the number density of B—O bonds contributing to the reaction in the glass is though to be given by subtracting the number density of bridging bonds between cations other than boron within the glass from the number density of boron bonds in the glass, that is, is thought to be qualitatively proportional to the number density of excess boron bonds. Accordingly, the smaller this value becomes, the more the reaction between boron and fluorine is suppressed, and the more the volatilization rate is reduced. A particularly marked effect is achieved by reducing this value to below zero. Accordingly, the lower the fluorine content and the fewer the excess B—O—B bonds that are present, the greater the suppression effect on volatilization. When this value is lower than 0, that is, when the quantity of oxygen bonded to boron is smaller than the quantity of oxygen bonded to other components, the effect is particularly pronounced. It is not just B×F, but rather D×F, that is desirably low.
FIG. 10 shows the change in weight reduction (volatilization) due to change in the F content in optical glasses of Forms A to D of the present invention, with the F content denoted by the horizontal axis and the change in weight denoted by the vertical axis. From this graph, it will be understood that the reduction in weight tends to increase as the F content increases. FIG. 11 shows the relation between the value of D and the reduction in weight for glasses with F contents of 7 to 9 percent, with the value of D denoted by the horizontal axis and the reduction in weight denoted by the vertical axis. FIG. 12 shows the relation between the value of D and the reduction in weight in optical glasses with F contents of 14 to 16 percent, with the value of D denoted by the horizontal axis and the reduction in weight denoted by the vertical axis. FIG. 14 combines FIGS. 12 and 13.
The reduction in weight is caused by volatilization from the glass melt, and is thus a quantitative indicator of volatilization. F sometimes volatizes alone, and sometimes cleaves the B—O—B bond formed in the glass network and volatizes in the form of molecules in which fluorine is bonded to other glass components, such as BF3 and BF2+. It is primarily the latter which cause serious volatilization striae and changes in characteristics over time during molding of the glass.
In the volatilization produced by fluorine, fluorine compounds that do not contain boron, such as SiF4, are also present. However, due to differences in their vapor pressure, most volatizing components can be thought of as being comprised of fluorine and boron (along with glass and atmospheric oxygen and hydrogen).
A comparison of the B—O—B bond with the B—O—X bond (where X denotes a cation other than B) in the glass network reveals that the probability of forming a volatile component in the B—O—B bond is greater when subjected to a replacement reaction of oxygen with fluorine caused by fluorine.
Since large numbers of B—O—B bonds present in glasses with high values of D, glasses with high values of D tend to undergo greater volatilization of components within the glass. However, despite the B network tending to cleave readily, volatile compounds tend not to be produced so long as the content of F is low.
Even when the F content is high, in a case when the value of D is low and cleavage of the B network tends not to occur, volatile compounds tend not to be produced.
Thus, the F content and the value of D are factors that greatly affect the level of volatilization.
Other than B, rare earth components, typified by La, are cations X that have a strong ability to retain both B and F within the glass without volatilization. Accordingly, as set forth further below, following the F content and the value of D, the value obtained by multiplying the BO1.5 content by the F content and then dividing the product by the LaO1.5 content—namely, (BO1.5×F)/LaO1.5—is conceivable as an indicator affecting the level of volatilization. Reducing (BO1.5×F)/LaO1.5 further suppresses volatilization.
From such perspectives, the upper and lower limits of excess B—O—B bonds: D are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. The value of excess B—O—B bonds: D can be suitably adjusted by adjusting the quantities of BO1.5, F, and other components that are incorporated into the optical glass.
(Computation Methods)


    BB=(quantity of BO1.5)×1.5
    BO=total quantity of oxygen
    D=BB—(BO—BB)
    The quantity of BO1.5 is the value when the content of BO1.5 is denoted as a cationic percentage.
    BO is the relative value of the quantity of O when the total quantity of all cations is adopted as 100.









TABLE 1-23







D (= BB − (BO − BB))














Form
Basic
A
B
C
D



















Upper limit
1
60
20

60
0




2
40
10

50
−10




3
20
5
20
40
−20




4
10
0
10
30
−25




5
5
−5
0
20
−30




6
0
−10
−10
15




7
−5

−15




8
−10

−20



Lower limit
1
−60
−60
−60
−20
−45




2
−40
−40
−50
−15
−50




3
−30
−30
−40
−10
−55




4
−25
−25
−35
−5
−60




5
−20
−20
−30
0










    BO1.5×F/LaO1.5 


In the glass of the present invention, in which LaO1.5 is an essential component, it is desirable to adjust BO1.5×F/LaO1.5, which is an indicator obtained by multiplying BO1.5 by F and dividing the product by LaO1.5, to further adjust the level of volatilization while maintaining a high refractive index and low dispersion. The incorporation of LaO1.5, which is capable of bonding both oxygen and fluorine, reduces the quantity of fluorine that actually contributes to volatilization. That is, the smaller BO1.5×F/LaO1.5 is made, the less volatilization occurs. The value of BO1.5×F/LaO1.5 can be suitably set by adjusting BO1.5, F, LaO1.5, and other components.







TABLE 1-24







BO1.5 × F/LaO1.5













Form
A
B
C
D

















Upper limit
1
45
42
48
18




2
42
40
45
15




3
40
38
42
13




4
38
35
40
11




5
35
33
38





6
30
30
35





7
25
28
30





8

25





Lower limit
1
5
3
8
1




2
8
5
10
2




3
10
8
14
3




4
14
10
18
5




5
18
14
22
8




6

18









SiO2/BO1.5, the ratio of the SiO2 content to the BO1.5 content, is an indicator of suppression of molding striae due to increased viscosity that desirably falls within a range of 0.10 to 0.40. Among glass network-forming components, the use of a large amount of viscosity-increasing SiO2 raises the viscosity during molding and suppresses deterioration of the internal quality of the glass due to the generation of striae. From such a perspective, the upper and lower limits of SiO2/BO1.5 are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. The value of SiO2/BO1.5 can be suitably set by adjusting the quantities of the components SiO2 and BO1.5 that are incorporated into the optical glass.







TABLE 1-25







SiO2/BO1.5














Form
Basic
A
B
C
D



















Upper limit
1
0.40
0.55
0.4
0.4
0.20




2
0.36
0.50
0.36
0.36
0.18




3
0.34
0.40
0.34
0.34
0.16




4
0.32
0.36
0.32
0.32
0.14




5
0.30
0.34
0.3
0.3
0.13




6
0.28
0.32
0.28
0.28




7

0.30
0.27
0.25




8

0.28



Lower limit
1
0.10
0.1
0
0.05
0.03




2
0.15
0.15
0.1
0.1
0.05




3
0.17
0.17
0.15
0.15
0.07




4
0.19
0.19
0.17
0.17
0.09




5
0.21
0.21
0.19
0.19
0.1




6
0.22
0.22
0.21
0.21
0.11




7
0.23

0.22




8
0.23










LaO1.5/ΣRe (ΣRe=total quantity of rare earth components), the ratio of the content of LaO1.5 to the total content of rare earth components, is an indicator of suppression of the formation of striae due to lowering of the liquidus temperature that desirably falls within a range of 0.30 to 0.80. Optimizing the ratio of rare earth components that raise the melting point of the glass lowers the melting point through an eutectic effect. This effect lowers the minimum temperature at which crystals precipitate out into the glass melt, or the liquidus temperature, thereby increasing the maximum viscosity at which the glass melt will flow out continuously. From such perspectives, the upper and lower limits of LaO1.5/ΣRe are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. The value of LaO1.5/ΣRe can be suitably set by adjusting the quantities of LaO1.5 and various rare earth components that are incorporated into the optical glass.







TABLE 1-26







LaO1.5/ΣRe














Form
Basic
A
B
C
D




















1
0.80
0.75
0.8
0.9
0.9




2
0.70
0.7
0.75
0.8
0.85




3
0.60
0.6
0.7
0.7
0.8




4
0.57
0.57
0.67
0.6
0.77




5
0.55
0.55
0.65
0.57
0.75




6
0.53
0.53
0.63
0.55




7
0.52
0.52
0.62



Lower limit
1
0.30
0.3
0.3
0.3
0.5




2
0.40
0.4
0.4
0.4
0.55




3
0.45
0.45
0.5
0.45
0.6




4
0.48
0.48
0.55
0.48
0.65




5
0.49
0.49
0.58

0.7




6


0.59










2LiO0.5+ZnO+(F/2)—the combined sum of twice the LiO0.5 content, the ZnO content, and 1⁄2 the F content—is an indicator of enhanced precision press moldability due to a decrease in the glass transition temperature Tg that desirably falls within a range of 20 to 60. The effect of lowering the Tg of a glass by incorporating Li, Zn, and F is 2 for Li, 1 for Zn, and 0.5 for F per atomic percent. Thus, the sum thereof, 2LiO0.5+ZnO+(F/2), is approximately linked to the glass transition temperature Tg of the glass. The magnitude of this indicator is an indicator of the ease of press molding. LiO0.5 and ZnO are values denoted as cationic percentages. F is the relative value of the quantity of F when the total quantity of all cations is adopted as 100. From such a perspective, the upper and lower limits of 2LiO0.5+ZnO+(F/2) are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. The value of 2LiO0.5+ZnO+(F/2) can be suitably set by adjusting the quantities of the components LiO0.5, ZnO, and F that are incorporated into the optical glass.
FIG. 5 shows how the Tg changes with change in 2LiO0.5+ZnO+(F/2), with the value of 2LiO0.5+ZnO+(F/2) be denoted by the horizontal axis and the value of the glass transition temperature Tg being denoted by the vertical axis. As will be clear from FIG. 5, the Tg can be lowered by increasing 2LiO0.5+ZnO+(F/2) and the Tg can be raised by decreasing 2LiO0.5+ZnO+(F/2).







TABLE 1-27







2LiO0.5 + ZnO + (F/2)














Form
Basic
A
B
C
D



















Upper limit
1
60
45

45
40




2
50
40
45
40
37




3
45
37
40
37
35




4
40
35
37
35
32




5
37
34
35
34




6
35

34




7
34




8



Lower limit
1
20
25
20
25
20




2
25
28
23
28
22




3
28
29
26
29
24




4
29
30
28
30
25




5
30
31
29
31
26




6
31

30

28










2LiO0.5/(2LiO0.5+ZnO)—the value of twice the LiO0.5 content divided by the combined sum of twice the LiO0.5 content and the ZnO content—contributes to enhancing glass characteristics (by the effects of suppressing a drop in νd and lowering the specific gravity) by adjusting Tg-lowering components and desirably falls within a range of 0.10 to 1.00. Among components that lower the glass transition temperature Tg of the glass, Li lowers νd less than Zn and has the effect of increasing the refractive index nd relative to the specific gravity of the glass obtained. It is thus employed to obtain a glass with a high refractive index, low dispersion, a low specific gravity, and a high kinematic viscosity. From such perspectives, the upper and lower limits of 2LiO0.5/(2LiO0.5+ZnO) are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. Further, the value of 2LiO0.5/(2LiO0.5+ZnO) can be suitably set by adjusting the quantities of the components LiO0.5 and ZnO that are incorporated into the optical glass.







TABLE 1-28







2LiO0.5/(2LiO0.5 + ZnO)














Form
Basic
A
B
C
D



















Upper limit
1
1.00
1.0
1.0

1.0




2
0.90
0.9
0.9

0.9




3
0.85
0.85
0.8

0.8




4


0.7

0.7




5


0.6

0.6




6


0.5

0.5




7


0.45

0.4




8


0.4



Lower limit
1
0.10
0.1
0
0.75
0




2
0.30
0.3
0.1
0.8
0.05




3
0.40
0.4
0.15
0.85
0.1




4
0.50
0.5
0.2
0.9
0.15




5
0.60
0.6
0.25
0.95
0.2




6
0.65
0.65
0.3
1
0.25




7
0.70
0.7




8
0.75
0.75










ZnO+3ZrO2+5TaO2.5, the combined sum of the Zn content, three times the ZrO2 content, and 5 five times the TaO2.5 content, is an indicator of the maintenance of low dispersion by controlling the quantities of high dispersion components that desirably falls within a range of 0 to 60.0. The effect of lowering the νd of a glass by incorporating Zn, Zr, and Ta into the glass is 1 for Zn, 3 for Zr, and 5 for Ta per atomic percent. Accordingly, the sum of ZnO+3ZrO2+5 TaO2.5 is approximately linked to the νd of the glass, so the magnitude of this indicator is an indicator of how low the dispersion is. It is also possible to include indicators such as W, Nb, and Ti that lower dispersion even more than Ta. However, as set forth above, the incorporation of large quantities of W, Nb, and Ti is undesirable. From such perspectives, the upper and lower limits of ZnO+3ZrO2+5TaO2.5 are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. The value of ZnO+3ZrO2+5TaO2.5 can be suitably set by adjusting the quantities of components ZnO, ZrO2, and TaO2.5 that are incorporated into the optical glass.







TABLE 1-29







ZnO + 3ZrO2 + 5TaO2.5














Form
Basic
A
B
C
D



















Upper limit
1
60.0
40
60
12
80




2
40.0
30
50
8
70




3
30.0
25
46
5
65




4
25.0
22
43
3
60




5
22.0
21
40
2
55




6
21.0
20.5
39
1




7
20.5
20
38.5
0




8
20.0

38



Lower limit
1
0.0
0


30




2
1.0
1
10

35




3
6.0
6
20

40




4
10.0
10
30

45




5
14.0
14
34

50




6
16.0
16
36




7
18.0
18
36.5










The glass transition temperature Tg (° C.) is an indicator of the degree of difficulty of precision press molding that desirably falls within a range of 200 to 590° C. A low glass transition temperature permits a low press molding temperature. It can be measured with a differential thermal analyzer DSC. From such perspectives, the upper and lower limits of the glass transition temperature Tg (° C.) are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. The glass transition temperature Tg (° C.) can be suitably set primarily by adjusting the quantities of the components LiO0.5, ZnO, and F that are incorporated into the optical glass. Further, microadjustment is possible by adjusting the quantities of the components SiO2 and TaO2.5 that are incorporated into the optical glass.







TABLE 2-1







Glass transition temperature Tg (° C.)












Form
Basic
A
B
C
D
















Upper limit
1
590
580
590
600
590



2
580
575
580
590
580



3
575
570
575
580
570



4
570
565
570
575
565



5
565
560
565
570
560



6
560
555
560
565



7
555
550
555
560



8
550
540
550



9
540

540


Lower limit
1
200
200
200
200
200



2
300
300
300
300
300



3
400
400
400
400
400



4



500



5



530









The liquidus temperature LT (° C.) is an indicator of glass stability that desirably falls within a range of 500 to 1,140° C. The minimum temperature at which no precipitation of crystals is observed when a glass melt is maintained in a furnace is defined as the liquidus temperature (LT). The liquidus temperature LT (° C.) (when the furnace temperature is set in increments of 10° C.) can be measured by placing 30 cc of glass in a platinum crucible, melting the glass for 10 to 20 minutes in a furnace at 1,200 to 1,250° C., homogenizing the melt by stirring, cooling the obtained glass in the crucible to below the glass transition temperature Tg, placing a platinum cover on the crucible, and maintaining the crucible in a furnace set to 1,050 to 1,140° C. for two hours to observe the crystals precipitating on the surface of the glass, within the glass, and at the interface of the glass and the inner wall of the crucible. From such a perspective, the upper and lower limits of the liquidus temperature LT (° C.) are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. The liquidus temperature LC (° C.) can be suitably set by adjusting the quantities of components that are incorporated into the optical glass, such as BO1.5 and SiO2, to enhance the thermal stability of the glass. The liquidus temperature can be lowered by improving the thermal stability of the glass. Within the composition ranges of the various forms, the liquidus temperature of the glass tends to decrease with improvement in thermal stability.







TABLE 2-2







Liquidus temperature LT (° C.)












Form
Basic
A
B
C
D
















Upper limit
1
1150
1120
1140
1120
1140



2
1120
1100
1120
1100
1120



3
1100
1090
1100
1090
1100



4
1090
1080
1090
1080
1090



5
1080
1070
1080
1070
1080



6
1070
1060
1070
1060
1070



7
1060
1050
1060
1050
1060



8
1050

1050

1050


Lower limit
1
500
500
500
500
500



2
600
600
600
600
600



3
700

700
700
700



4



800









λ(lambda) 80, λ70, and λ5 (nm) are wavelengths (nm) at which 80 percent, 70 percent, and 5 percent transmittance to the exterior, respectively, are exhibited by a sample 10 mm in thickness. From the perspective of inhibiting specific wavelength dependence in a particular glass, at a minimum, the external transmittance from λ80 to 1,550 nm is desirably not lowered to 25 percent or below, preferably 50 percent or below, more preferably 70 percent or below, still more preferably 75 percent or below, and yet more preferably, 80 percent or below. The external transmittance at λ80, λ70, λ5 (nm), and the wavelength range of λ80 to 1,555 nm, can be suitably adjusted by adjusting the quantities of various components with different ultraviolet absorption edges that are incorporated into an optical glass; limiting the quantities of impurities in the form of such color-producing elements as Fe, Cr, Mn, Co, and Ni; incorporating various oxidizing gas components (NO3 and the like); and reducing gas components (NH4 and the like). Thus, it is desirable not to incorporate any Fe, Cr, Mn, Co, or Ni, and to limit the quantities of impurities in the form of Fe, Cr, Mn, Co, and Ni that are mixed in.







TABLE 2-3







λ80












Form
Basic
A
B
C
D
















Upper limit
1

450
450
450
550



2

400
400
400
500



3

380
380
380
470



4




450


Lower limit
1

300
300
300
350



2

330
330
330
370



3

350
350
350
400
















TABLE 2-4







λ70












Form
Basic
A
B
C
D
















Upper limit
1

450
450
450
500



2

400
400
400
450



3

370
370
370
400



4




370


Lower limit
1

250
250
250
300



2

300
300
300
330



3

320
320
320
350








350
















TABLE 2-5







λ5












Form
Basic
A
B
C
D
















Upper limit
1

350
350
350
450



2

320
320
320
400



3

290
290
290
350


Lower limit
1

200
200
200
250



2

250
250
250
300



3

270
270
270
320








330









The value (kinematic viscosity) (10−4 m2/s=St) obtained by dividing the viscosity at the liquidus temperature by the density at room temperature is an indicator of the moldability of the glass melt that desirably falls within a range of 0.20 to 1,000 (St). It is obtained by dividing the viscosity at the liquidus temperature, η(eta)LT(P) by the specific gravity (g/cc). It corresponds to the flow rate as the glass flows out of a pipe or the like under its own weight, and serves as a yardstick of the ease with which the glass melt can be molded. Considering the specific gravity of the glass facilitates comparison of glasses with different specific gravities and their flow rates. From such perspectives, the upper and lower limits of the value obtained by dividing the viscosity at the liquidus temperature by the density at room temperature are suitably set as indicated below. The value of the kinematic viscosity can be suitably set by adjusting the quantities of the various components that are incorporated into the optical glass, such as BO1.5, which has the effect of improving the thermal stability of the glass, and SiO2, which has the effects of increasing the viscosity of the glass while similarly improving the thermal stability of the glass. Improving the thermal stability of the glass lowers the liquidus temperature and increases the viscosity at the liquidus temperature. As compared to rare earth components, BO1.5 and SiO2 have the additional function of reducing the specific gravity of the glass. Thus, increasing the quantities of BO1.5 and SiO2 that are incorporated increases the kinematic viscosity.







TABLE 2-6







Kinematic viscosity at liquidus temperature (St)












Form
Basic
A
B
C
D
















Upper limit
1
1000
30
30
30
30



2
300
10
10
10
10



3
100
3
3
3
3



4
30
1
1
1
1



5
10



6
3



7
1



8


Lower limit
1
0.2
0.4
0.4
0.4
0.2



2
0.4
0.5
0.5
0.5
0.4



3
0.5
0.55
0.55
0.55
0.5



4
0.55
0.6
0.6
0.6
0.55



5
0.6
0.65
0.65
0.65
0.6



6
0.65
0.7
0.7
0.7
0.65



7
0.7
0.75
0.75
0.75
0.7



8
0.75

0.8
0.8
0.8









The quantity of glass flowing per unit time, that is, the flow rate, is proportional to the density of the glass and is inversely proportional to the viscosity of the glass. Accordingly, the inverse of the value of the kinematic viscosity is proportional to the flow rate. Thus, the inverse of the kinematic viscosity is an indicator of the flow rate.
FIG. 6 shows the change in the inverse of the kinematic viscosity and the change in the viscosity relative to the change in temperature in an example of the optical glass of the present invention, with temperature being denoted by the horizontal axis, viscosity of the glass being denoted by the left vertical axis, and the inverse of the kinematic viscosity, that is, an indicator of the flow rate, being denoted by the right vertical axis.
In FIG. 6, it will be understood that the amount of increase in the indicator of the flow rate (the inverse of the kinematic viscosity) due to a decrease of 1 dPa·s in viscosity was small in the region of relatively high viscosity (such as a viscosity of equal to or greater than 10 dPa·s, that is, at equal to or below 940° C.).
However, in the region of relatively low viscosity (such as a viscosity of 5 dPa·s, 3 dPa·s, or the like), the amount of increase in the indicator of the flow rate (the inverse of the kinematic viscosity) due to a decrease of 1 dPa·s in viscosity increased. Thus, even for a difference in the viscosity value of just 0.5 or 1.0 dPa·s, the corresponding change in the flow rate was substantial, greatly affecting glass moldability. In glasses with a liquidus temperature exceeding 1,050° C., or of 1,100° C. or higher, that is, in glasses in which the viscosity at the liquidus temperature is low like above, the reason a change of just 10° C. in liquidus temperature greatly affects moldability is due to such facts.







TABLE 2-7







Viscosity at liquidus temperature (dPa · s)












Form
Basic
A
B
C
D
















Upper limit
1
5000
5000
5000
5000
5000



2
1500
1500
1500
1500
1500



3
500
500
500
500
500



4
150
150
150
150
150



5
50
50
50
50
50



6
15
15
15
15
15



7
5
5
5
5
5


Lower limit
1
1
1
1
1
1



2
2
2
2
2
2



3
2.5
2.5
2.5
2.5
2.5



4
2.75
2.75
2.75
2.75
2.75



5
3
3
3
3
3



6
3.25
3.25
3.25
3.25
3.25



7
3.5
3.5
3.5
3.5
3.5



8
3.75
3.75
3.75
3.75
3.75









When the viscosity is low at the liquidus temperature, problems tend to occur in that striae tend to form, it becomes difficult to control the flow of glass, and the like. When the viscosity is high at the liquidus temperature, the glass flow rate drops, productivity decreases, or the holding time of the glass melt in the melting furnace becomes excessively long, causing variation in various characteristics.
The optical glass of the present invention is suited to lenses with large diameters that are employed in single-lens reflex cameras and the like. Thus, a low specific gravity is desirable. From such perspectives, the upper and lower limits of the specific gravity are suitably set as indicated below. The specific gravity can be measured by Archimedes' method. The specific gravity can be suitably set by adjusting the quantities of various components of relatively low molecular weight, such as BO1.5 and SiO2, and rare earth components of relatively high molecular weight that are incorporated into the optical glass.







TABLE 2-8







Specific gravity














Form
Basic
A
B
C
D



















Upper limit
1
6.00

6
5.30
6




2
5.50
5.5
5.8
5.10
5.9




3
5.30
5.30
5.6
5.00
5.8




4
5.10
5.10
5.5
4.90
5.7




5
5.00
5.00
5.4
4.80
5.6




6
4.90
4.90
5.3
4.70




7
4.80
4.80
5.2
4.60




8
4.70
4.70
5.1
4.5



Lower limit
1
2.0
2.0
2
2.0




2
3.0
3.0
3
3.0
4




3
4.0
4.0
4
3.5
4.5




4
4.5
4.5
4.5
3.8
5




5
4.6
4.6
5
4.0










The degrees of the refractive index and dispersion: nd−(2.25−0.01×νd)

The optical glass of the present invention is of high refractive index and low dispersion. The degrees thereof are desirably a refractive index that lies above and a dispersion that lies below a line drawn connecting (nd, νd)=(1.80, 45) and (1.75, 50) in a plot of nd−νd in which nd is denoted by the horizontal axis and νd is denoted by the vertical axis. Further, a certain quantity of glass forming components is required to maintain moldability of the glass. Thus, glass compositions in which the refractive index is so high and the dispersion so low that glass moldability is lost are undesirable. From such perspectives, the upper and lower limits of nd−(2.25−0.01×νd) are suitably set as indicated below for the basic forms and Forms A, B, C, and D of the present invention. nd−(2.25−0.01×νd) can be computed from the refractive index nd and the Abbé number νd. The value of nd−(2.25−0.01×νd) increases with the quantity of rare earth components and decreases with increases in the quantities of BO1.5, ZnO, ZrO2, TaO2.5, and the like, and can thus be suitably set by adjusting the quantities of these components that are incorporated into the optical glass.







TABLE 2-9







nd − (2.25 − 0.01 × νd)












Form
Basic
A
B
C
D
















Upper limit
1
0.050
0.040
0.040
0.040
0.040



2
0.040
0.030
0.030
0.030
0.030



3
0.030
0.025
0.025
0.025
0.025



4
0.025
0.022
0.022
0.022
0.022



5
0.022
0.020
0.021

0.019



6
0.020

0.020

0.016



7




0.014



8




0.013


Lower limit
1

−0.010
−0.010
−0.010
−0.010



2

−0.005
−0.005
−0.005
−0.005



3
0.000
0.000
0.000
0.000
0.000



4
0.005
0.005
0.005
0.005
0.002



5
0.008
0.008
0.010
0.008
0.004



6
0.010
0.010
0.012
0.010
0.006



7
0.012
0.012
0.014
0.012
0.008



8
0.013
0.013
0.016
0.013
0.009



9
0.014
0.014
0.017
0.014



10
0.015

0.018
0.015









The shift away from the stoichiometric ratio (oxygen+fluorine/2)/cations (molar ratio)

Fluorine ions are primarily introduced into the glass by replacing a certain cationic percentage of oxides with fluorides. In this process, to inhibit coloration and the like due to lattice defects typified by oxygen defects and cation defects in the glass, the cations and anions in the glass are desirably introduced in a form that maintains charge neutrality in the glass. Accordingly, components employed to manufacture the glass are desirably incorporated so as to maintain the stoichiometric ratio of the glass by replacing one oxygen atom with two fluorine atoms, and so forth. From such perspectives, the upper and lower limits of the shift in the stoichiometric ratio are suitably set as indicated below. It can be calculated from the molar percentage of oxygen ions, the molar percentage of fluorine ions, and the total of cationic percentage. The shift away from the stoichiometric ratio can be suitably set by incorporating various oxidizing gas components (such as NO3), reducing gas components (such as NH4), and the like when transition metal oxides (such as ZrO2, TaO2.5, TiO2, NbO2.5, and WO3) are being incorporated. Almost no shift away from the stoichiometric ratio occurs when incorporating typical metal oxides.








TABLE 2-10







Desirable upper limit
Stoichiometric ratio ± 0.1


Preferable upper limit
Stoichiometric ratio ± 0.05


More preferable upper limit
Stoichiometric ratio ± 0.01


Still more preferable upper limit
Substantially equal to stoichiometric



ratio









The molar percentage of oxygen ions defines the unit oxygen number (for example: the oxygen number of BO1.5 is 1.5) per cation contained in the chemical formula of each component for introducing cations. The oxygen ion/cation (molar ratio) is the cationic percentages in the glass multiplied by the sum of the unit oxygen, divided by the sum of the cationic percentages, expressed as a percentage. Similarly, the molar percentage of fluorine ions is the sum of the ion percentages of the fluorine incorporated into the glass, divided by the sum of the cationic percentages, expressed as a percentage. From such perspectives, the upper and lower limits are suitably set as indicated below. They can be calculated from the molar percentage of oxygen ions and from the cationic percentages. The oxygen ion/cation (molar ratio) can be suitably set by incorporating various oxidizing gas components (such as NO3), reducing gas components (such as NH4), and the like when incorporating glass components in the form of transition metal oxides (such as ZrO2, TaO2.5, TiO2, NbO2.5, and WO3). The oxygen ion/cation (molar ratio) increases with the quantity of cations of high valence that are included among the glass components, but tends to decrease as the F/O ratio increases.







TABLE 2-11







Oxygen ion/cation (molar ratio)














Form
Basic
A
B
C
D



















Upper limit
1
2.0
2.0
2.0
2.0
2.0




2
1.8
1.8
1.8
1.8
1.8




3
1.7
1.7
1.7
1.7
1.7




4
1.6
1.6
1.6
1.6
1.6




5
1.5
1.5
1.5
1.5
1.5



Lower limit
1
0.5
0.5
0.5
0.5
0.5




2
0.8
0.8
0.8
0.8
0.8




3
1.0
1.0
1.0
1.0
1.0




4
1.1
1.1
1.1
1.1
1.1




5
1.2
1.2
1.2
1.2
1.2




6
1.3
1.3
1.3
1.3
1.3










The change in nd over time: Δ(DELTA)nd(/hr)

The change in the refractive index over time is a measurement value obtained from various measured values of the refractive index and a sampling time interval by sampling the glass melt during melting, measuring the refractive index nd of the glass sample, allowing a prescribed interval of time to elapse following the sampling, sampling the glass melt again, measuring the refractive index nd of the glass sample, and repeating this operation. The change in the refractive index over time can be reduced by reducing excess B—O—B bonds and reducing BO1.5×F/O, which is the quantity of volatile components. From such perspectives, the upper and lower limits of the change in the refractive index over time, Δnd(/hr), are suitably set as indicated below. The change in nd over time is caused by the change, albeit slight, in the glass composition due to volatilization from the glass melt Inhibiting this volatilization can reduce the change in refractive index nd over time. The level of volatilization can be adjusted by adjusting the quantities of various components incorporated into the optical glass, including BO1.5 and F. The quantities of BO1.5 and F that are incorporated into the optical glass have the greatest effect on the level of volatilization.












TABLE 2-12





Form
Basic
A
B
C
D





















Upper limit
1
0.00200
0.00200
0.00200
0.00200
0.00200



2
0.00100
0.00100
0.00100
0.00100
0.00100



3
0.00080
0.00080
0.00080
0.00080
0.00080



4
0.00060
0.00060
0.00060
0.00060
0.00060



5
0.00040
0.00040
0.00040
0.00040
0.00040



6
0.00030
0.00030
0.00030
0.00030
0.00030



7
0.00020
0.00020
0.00020
0.00020
0.00020



8
0.00010
0.00010
0.00010
0.00010
0.00010



9
0.00005
0.00005
0.00005
0.00005
0.00005












Lower limit 1
0.00000
0.00000
0.00000
0.00000
0.00000









The change in Tg over time: Δ(DELTA)Tg (° C./hr)

The change in Tg over time is a measurement value obtained from various measured values of the glass transition temperature Tg and a sampling time interval by sampling the glass melt during melting, measuring the glass transition temperature Tg of the glass sample, allowing a prescribed interval of time to elapse following the sampling, sampling the glass melt again, measuring the glass transition temperature Tg of the glass sample, and repeating this operation. The change in Tg over time can be reduced by reducing excess B—O—B bonds and reducing BO1.5×F/O, which is the quantity of volatile components. From such perspectives, the upper and lower limits of the change in Tg over time, ΔTg (° C./hr), are suitably set as indicated below. The change in Tg over time is caused by the change, albeit slight, in the glass composition due to volatilization from the glass melt Inhibiting this volatilization can reduce the change in the glass transition temperature Tg over time. The level of volatilization can be adjusted by adjusting the quantities of various components incorporated into the optical glass, including BO1.5 and F. The quantities of BO1.5 and F that are incorporated into the optical glass have the greatest effect on the level of volatilization.












TABLE 2-13





Form
Basic
A
B
C
D





















Upper limit
1
5
5
5
5
5



2
3
3
3
3
3



3
2
2
2
2
2



4
1
1
1
1
1



5
0.8
0.8
0.8
0.8
0.8



6
0.5
0.5
0.5
0.5
0.5



7
0.3
0.3
0.3
0.3
0.3



8
0.1
0.1
0.1
0.1
0.1












Lower limit 1
0.00000
0.00000
0.00000
0.00000
0.00000









The change in specific gravity over time: Δ(DELTA)specific gravity(/hr)

The change in specific gravity over time is a measurement value obtained from various measured values of the specific gravity and a sampling time interval by sampling the glass melt during melting, measuring the specific gravity of the glass sample, allowing a prescribed interval of time to elapse following the sampling, sampling the glass melt again, measuring the specific gravity of the glass sample, and repeating this operation. The change in specific gravity over time can be reduced by reducing excess B—O—B bonds and reducing BO1.5×F/O, which is the quantity of volatile components. From such perspectives, the upper and lower limits of the change in specific gravity over time, Δspecific gravity(/hr), are suitably set as indicated below. The change in specific gravity over time is caused by the change, albeit slight, in the glass composition due to volatilization from the glass melt Inhibiting this volatilization can reduce the change in specific gravity over time. The level of volatilization can be adjusted by adjusting the quantities of various components incorporated into the optical glass, including BO1.5 and F. The quantities of BO1.5 and F that are incorporated into the optical glass have the greatest effect on the level of volatilization.












TABLE 2-14





Form
Basic
A
B
C
D





















Upper limit
1
0.01
0.01
0.01
0.01
0.01



2
0.008
0.008
0.008
0.008
0.008



3
0.005
0.005
0.005
0.005
0.005



4
0.003
0.003
0.003
0.003
0.003



5
0.002
0.002
0.002
0.002
0.002



6
0.0015
0.0015
0.0015
0.0015
0.0015



7
0.001
0.001
0.001
0.001
0.001



8
0.0005
0.0005
0.0005
0.0005
0.0005












Lower limit 1
0.00000
0.00000
0.00000
0.00000
0.00000









The change in the liquidus temperature over time: Δ(DELTA)LT(° C./hr)

The change in the liquidus temperature over time is a measurement value obtained from various measured values of the liquidus temperature and a sampling time interval by sampling the glass melt during melting, measuring the liquidus temperature of the glass sample, allowing a prescribed interval of time to elapse following the sampling, sampling the glass melt again, measuring the liquidus temperature of the glass sample, and repeating this operation. The change in liquidus temperature over time can be reduced by reducing excess B—O—B bonds and reducing BO1.5×F/O, which is the quantity of volatile components. From such perspectives, the upper and lower limits of the change in liquidus temperature over time, ΔLT (° C./hr), are suitably set as indicated below. The change in liquidus temperature over time is caused by the change, albeit slight, in the glass composition due to volatilization from the glass melt Inhibiting this volatilization can reduce the change in the liquidus temperature over time. The level of volatilization can be adjusted by adjusting the quantities of various components incorporated into the optical glass, including BO1.5 and F. The quantities of BO1.5 and F that are incorporated into the optical glass have the greatest effect on the level of volatilization.












TABLE 2-15





Form
Basic
A
B
C
D





















Upper
1
10
10
10
10
10


limit
2
8
8
8
8
8



3
6
6
6
6
6



4
4
4
4
4
4



5
3
3
3
3
3



6
2
2
2
2
2



7
1
1
1
1
1












Lower
0.00000
0.00000
0.00000
0.00000
0.00000


limit 1









The change in kinematic viscosity over time: Δ(DELTA)kinematic viscosity (m3/s/hr)

The change in the kinematic viscosity over time is a measurement value obtained from various measured values of the kinematic viscosity and a sampling time interval by sampling the glass melt during melting, measuring the kinematic viscosity of the glass sample, allowing a prescribed interval of time to elapse following the sampling, sampling the glass melt again, measuring the kinematic viscosity of the glass sample, and repeating this operation. The change in kinematic viscosity over time can be reduced by reducing excess B—O—B bonds and reducing BO1.5×F/O, which is the quantity of volatile components. From such perspectives, the upper and lower limits of the change in kinematic viscosity over time, Akinematic viscosity (m3/s/hr), are suitably set as indicated below. The change in kinematic viscosity over time is caused by the change, albeit slight, in the glass composition due to volatilization from the glass melt Inhibiting this volatilization can reduce the change in the kinematic viscosity over time. The level of volatilization can be adjusted by adjusting the quantities of various components incorporated into the optical glass, including BO1.5 and F. The quantities of BO1.5 and F that are incorporated into the optical glass have the greatest effect on the level of volatilization.












TABLE 2-16





Form
Basic
A
B
C
D





















Upper limit
1
1.0
1.0
1.0
1.0
1.0



2
0.8
0.8
0.8
0.8
0.8



3
0.6
0.6
0.6
0.6
0.6



4
0.4
0.4
0.4
0.4
0.4



5
0.2
0.2
0.2
0.2
0.2



6
0.1
0.1
0.1
0.1
0.1



7
0.05
0.05
0.05
0.05
0.05



8
0.02
0.02
0.02
0.02
0.02



9
0.01
0.01
0.01
0.01
0.01












Lower limit 1
0.00000
0.00000
0.00000
0.00000
0.00000









The refractive index in the present invention is represented by the refractive index nd in the d line. The fraction is represented by the Abbé number, νd.

The lower limit of the refractive index in the first and second basic forms of the present invention is, in order of increasing desirability, 1.70, 1.73, 1.75, 1.76, and 1.765. Achieving a high refractive index facilitates the achievement of high functionality and compactness in optical elements. The upper limit of the refractive index nd in the first and second basic forms of the present invention is, in order of increasing desirability, 1.90, 1.87, 1.83, 1.81, 1.79, and 1.78. Not employing an excessively high refractive index facilitates the maintaining of a low glass transition temperature and the maintaining of a glass with good thermal stability.
The lower limit of the Abbé number νd in the first and second basic forms of the present invention is, in order of increasing desirability, 36, 39, 43, 46, 48, 49, and 49.3. The use of a glass with low dispersion permits the realization of an optical glass that is better suited to the correction of chromatic aberration. The lower upper limit of the Abbé number νd in basic optical glasses of the first and second forms of the present invention is, in order of increasing desirability, 55, 54, 53, 52, 51, 50.5, 50, and 49.8. This is because an excessively high Abbé number tends to make it difficult to maintain the thermal stability of the glass and low glass transition temperature characteristics.
Form A is an optical glass having a refractive index nd of 1.75 to 1.81 and an Abbé number νd of 48 to 52.
Form B is an optical glass having a refractive index nd of 1.79 to 1.835 and an Abbé number νd of 42 to 48.
Form C is an optical glass having a refractive index nd of 1.675 to 1.76 and an Abbé number νd of 51 to 58.
Form D is an optical glass having a refractive index nd of 1.825 to 1.90 and an Abbé number νd of 35 to 43.
Desirable refractive indexes nd and Abbé numbers νd for the various forms are indicated below.







TABLE 2-17







Refractive index nd













Form
A
B
C
D

















Upper limit
1
1.81
1.835
1.76
1.90




2
1.80
1.825
1.755
1.895




3
1.795
1.82
1.75
1.89




4
1.79
1.815
1.745
1.885




5
1.785
1.81
1.74





6
1.78
1.805
1.735




Lower limit
1
1.750
1.79
1.675
1.825




2
1.755
1.795
1.680
1.83




3
1.76
1.8
1.690
1.835




4
1.765
1.802
1.700
1.84




5

1.803
1.710
1.845




6


1.720
1.855




7


1.725
1.865




8



1.875
















TABLE 2-18







Abbé number νd













Form
A
B
C
D

















Upper limit
1
52.0
48
58.0
43.0




2
51.0
47.5
57.0
42.0




3
50.5
47
56.0
41.5




4
50.0
46.8
55.0
41.0




5
49.8
46.7
54.7
40.5




6

46.6
54.4
40







54.2
39




7



38



Lower limit
1
48
42
51
35




2
48.5
44
52
35.5




3
49
45
52
36




4
49.3
45.5
53
36.5




5

46
53
37




6

46.3
54









Both the above desirable refractive indexes and Abbé numbers can be realized in optical glasses that suitably combine any of the composition ranges specified in Tables 1-1 to 1-28 above and any of the characteristic ranges specified in Tables 2-1 to 2-18.
The optical glasses of the first basic form, second basic form, and Forms A, B, C, and D of the present invention can be obtained by procuring starting materials such as boric acid, oxides, and as needed, carbonates, nitrates, sulfates, and hydroxides; weighing out to achieve the desired characteristics, blending, and thoroughly stirring the various starting materials; charging the mixture to a melting vessel such as a platinum crucible; heating, melting, clarifying, and homogenizing the mixture; and molding the melt. To obtain a homogeneous glass, a melting temperature of, for example, 1,100 to 1,400° C. is desirable.
Alternatively, starting materials such as boric acid, oxides, and as needed, carbonates, nitrates, sulfates, and hydroxides can be rough melted to fabricate various cullets; the cullets can be blended to obtain desired characteristics, heated, melted, clarified, and homogenized; and the melt can be molded.
[The Preform for Precision Press-Molding]
The present invention includes a preform for precision press molding that is comprised of an optical glass of the first basic form, second basic form, or Form A, B, C, or D of the present invention.
A precision press-molding preform is a premolded glass material for use in the widely known precision press molding method.
The “precision press-molding preform” will sometimes be referred to simply as a “preform” hereinafter. The term “preform” refers to a premolded glass member that is heated for use in precision press molding. Here, the term “precision press-molding” is the method of forming the optically functional surfaces of an optical element by transfer from the molding surfaces of a pressing mold, also called mold optics molding, as is widely known. In optics, the term “optically functional surface” means a surface that refracts, reflects, diffracts, or permits the entering or exiting of, light that is being controlled. The surface of a lens or the like corresponds to such an optically functional surface.
During precision press molding, to permit good extension of the glass along the molding surface while preventing reaction and fusion of the glass to the pressing mold, the surface of the preform is desirably coated with a mold release film. Mold release films come in the form of noble metals (platinum, platinum alloys), oxides (oxides of Si, Al, Zr, La, Y, and the like), nitrides (nitrides of B, Si, Al, and the like), and carbon-containing films. A carbon-containing film comprised chiefly of carbon (in which the carbon content is greater than the content of other elements when the contents of the elements in the film are denoted as atomic percentages) is desirable as a carbon-containing film. Specific examples are carbon films and hydrocarbon films. A known method employing carbon as starting material, such as vacuum deposition, sputtering, and ion plating; or a known method employing a hydrocarbon or the like as the material gas, such as thermal decomposition, may be employed to form a carbon-containing film. Other films may be formed by deposition, sputtering, ion plating, the sol gel method, or the like.
The method of fabricating the preform of the present invention is not limited. However, it is desirably manufactured by the following methods utilizing the advantageous properties of the above-described glasses.
The first method of manufacturing a precision press-molding preform (referred to as preform manufacturing method I) is a method for manufacturing a precision press-molding preform by melting a glass starting material, causing the glass melt obtained to flow out, separating a glass melt gob, and molding the glass melt gob in a cooling step, and is characterized by the molding of a preform comprised of the above-described optical glass.
The second method of manufacturing a precision press-molding preform (referred to as preform manufacturing method II) is a method for manufacturing a precision press-molding preform by melting a glass starting material, molding the glass melt obtained to fabricate a molded glass member, and processing the molded member to fabricate a preform comprised of the optical glass of the present invention.
Both preform manufacturing methods I and II share the step of fabricating a homogenous glass melt from a glass starting material. For example, glass starting materials blended to yield desired characteristics are charged to a melting vessel made of platinum, and heated, melted, clarified, and homogenized to prepare a homogeneous glass melt. The glass melt is then caused to flow out of an outflow nozzle or an outflow pipe made of platinum or a platinum alloy the temperature of which has been adjusted. It is also possible to rough melt the glass starting materials to fabricate cullets; blend the cullets obtained; heat, melt, clarify, and homogenize to obtain a homogeneous glass melt; and cause the glass melt to flow out through the above-mentioned outflow nozzle or outflow pipe.
When forming small preforms or spherical preforms, the glass melt is made to drip out of the outflow nozzle in the form of a glass melt droplet of desired weight. This is then received in a preform-forming mold and molded into a preform. Alternatively, a glass melt droplet of desired weight is similarly made to drip out through an outflow nozzle into liquid nitrogen or the like to form a preform. When fabricating medium- or large-sized preforms, a glass melt flow is made to flow out of an outflow pipe, the front end of the glass melt flow is received by a preform-forming mold, a constriction is formed between the nozzle of the glass melt flow and the preform-forming mold, and the preform-forming mold is quickly lowered directly downward, allowing the surface tension of the glass melt to separate the glass melt flow at the site of the constriction. A glass melt gob of prescribed weight is then received in a receiving member and molded into a preform.
In order to fabricate a preform having a smooth surface that is free of scratches, grime, wrinkles, surface deformation, and the like, such as a free surface, it is possible to employ a method such as molding a glass melt gob into a preform while it is being floated by air pressure on a preform-forming mold or the like, or a method in which a glass melt droplet is placed in a medium such as liquid nitrogen that has been rendered liquid by cooling a gaseous material at the ordinary temperature and pressure, whereby a preform is molded.
When molding a glass melt gob into a preform while it is being floated, a gas (referred to as a “floating gas”) is blown onto the glass melt gob to apply upward air pressure. In this process, if the viscosity of the glass melt gob is excessively low, the floating gas penetrates into the glass, forming bubbles that remain in the preform. However, imparting a viscosity of 3 to 60 dPa·s to the glass melt gob floats the glass gob without the floating gas penetrating into the glass.
Examples of gases that can be employed in the course of blowing floating gas onto a preform are: air, N2 gas, O2 gas, Ar gas, He gas, steam and the like. The air pressure is not specifically limited other than that it be adequate to float the preform without it coming into contact with solid objects such as the surface of the forming mold.
The precision press-molded article (such as an optical element) that is fabricated from a preform will often have an axis of rotational symmetry such as is found in a lens. Thus, the shape of the preform desirably has an axis of rotational symmetry. Specific examples are spheres and items having a single axis of rotational symmetry. Examples of shapes having a single axis of rotational symmetry are items having smooth contour lines, free of edges and pits, in a cross-section containing the axis of rotational symmetry, such as an item having an ellipse the short axis of which conforms to the axis of rotational symmetry in the above cross-section. A shape in the form of an oblate sphere (a shape in which one axis running through the center of the sphere is established, and the dimensions are contracted in the direction of this axis) is another example.
In preform manufacturing method 1, the glass is molded within a temperature range permitting plastic deformation. Thus, a preform can be manufactured by press molding a glass gob. In that case, the shape of the preform can be set relatively freely, and can thus approximate the shape of the targeted optical element. For example, molding is possible where one of two opposing surfaces is made convex and the other concave, both surfaces are made concave, one surface is made flat and the other convex, one surface is made flat and the other concave, and both surfaces are made convex.
The surface of a preform thus fabricated can be coated with a carbon-containing film. However, the fluorine-containing optical glass of the present invention has a low glass transition temperature, permitting a low press molding temperature. Thus, it is not necessary to apply a carbon-containing film.
In preform manufacturing method 2, for example, after molding the glass melt by casting in a casting mold, strain of the molded member is removed by annealing, the molded member is cut or severed to split it into prescribed dimensions or shapes, multiple glass pieces are fabricated, and the glass pieces are polished to render their surfaces smooth, yielding preforms comprised of a prescribed weight of glass. The surface of a preform thus fabricated is also desirably coated with a carbon-containing film for use. Preform manufacturing method 2 is suited to the manufacturing of spherical preforms, platelike preforms, and the like that can be readily ground and polished.
In both of these manufacturing methods, the thermal stability of the optical glass employed is good. This permits the stable manufacturing of high-quality preforms with a tendency not to produce products that are defective because of glass devitrification, striae, or the like, and enhances the overall large-quantity production properties of the process of manufacturing optical elements.
Preforms that are preferred because they enhance the large-quantity production properties of optical elements by precision press molding will be described next.
From the aspect of a glass material, the optical glass of the present invention provides excellent precision press-molding properties. Reducing the amount of deformation of the glass in precision press molding permits lowering the temperature of the glass and the pressing mold during precision press molding, reducing the time required for press molding, and reducing the pressure applied during pressing. As a result, reactivity between the glass and the surface of the pressing mold decreases, the above problems occurring during precision press molding decrease, and large-quantity production properties improve.
The preforms that are desirably employed when precision press molding lenses have mutually opposing pressed surfaces (surfaces that are pressed by opposing molding surfaces in the mold during precision press molding). Preforms having an axis of rotational symmetry that runs through the center of the two pressed surfaces are preferred. Among such preforms, those that are suited to the precision press molding of meniscus lenses are those in which one pressed surface is convex and the other is concave, flat, or convex having a curvature that is less than the first convex surface.
In preforms that are suited to the precision press molding of biconcave lenses, one pressed surface is convex, concave, or flat, and the other surface is convex, concave, or flat.
In preforms that are suited to the precision press molding of biconvex lenses, one pressed surface is convex and the other surface is convex or flat.
In both cases, a preform with a shape approximating the shape of the article being precision press molded is desirable.
When molding a glass melt gob into a preform with a preform-forming mold, the lower surface of the glass on the pressing mold is approximately determined by the shape of the molding surface of the pressing mold. Additionally, the shape of the upper surface of the glass is determined by the surface tension of the glass melt and the weight of the glass itself. To reduce the amount of deformation of the glass during precision press molding, it is necessary to also control the shape of the upper surface of the glass during molding in the preform-forming mold. The shape of the upper surface of the glass determined by the surface tension of the glass melt and the weight of the glass itself is a free surface that is convex in shape. However, pressure can be applied to the upper surface of the glass to render it flat, concave, or convex with less curvature than the free surface. Specifically, the upper surface of the glass is molded to the desired shape by pressing with a pressing mold having a molding surface of desired shape, or by applying air pressure to the upper surface of the glass. In the course of pressing the upper surface of the glass with a pressing mold, multiple gas blow-holes can be provided in the molding surface of the forming mold, gas can be blown through the gas blow-holes to form a gas cushion between the molding surface and the upper surface of the glass, and the upper surface of the glass can be pressed through this gas cushion. Alternatively, when it is desirable to mold the upper surface of the glass into a surface of greater curvature than the free surface, negative pressure can be generated in the vicinity of the upper surface of the glass to mold the upper surface in a more mounded fashion.
A preform with a polished surface is also desirable to obtain a preform with a shape more closely approximating the shape of the article being precision press molded. For example, a preform in which one pressed surface is polished to be either flat or partially spherical, and the other pressed surface is polished so as to be partially spherical or flat, is desirable. The partially spherical portion of the surface can be either convex or concave. Whether to make it convex or concave is desirably determined based on the shape of the article being precision press molded, as set forth above.
The various preforms described above are desirable for molding lenses with diameters of 10 mm or greater and preferred for molding lenses with diameters of 20 mm or greater. They are also desirable for molding lenses with a center thickness exceeding 2 mm.
[The Optical Element]
The optical element of the present invention will be described next.
The optical element of the present invention is comprised of the optical glass of the above-described first basic form, second basic form, or Form A, B, C, or D.
The type of optical element itself is not specifically limited. Examples of typical elements are lenses such as aspherical lenses, spherical lenses, plano-concave lenses, plano-convex lenses, biconcave lenses, biconvex lenses, convex meniscus lenses, and concave meniscus lenses; microlenses; lens arrays; lenses with diffraction gratings; prisms; and prisms with lens functions. Examples of desirable optical elements are lenses such as convex meniscus lenses, concave meniscus lenses, biconvex lenses, biconcave lenses, plano-convex lenses, and plano-concave lenses; prisms; and diffraction gratings. Each of these lenses may be asymmetrical or spherical. As required, an antireflective coating, partially reflective coating with wavelength selecting properties, or the like may be provided on the surface.
The optical element of the present invention is comprised of glass with a high refractive index and low dispersion characteristics. It can thus be combined with optical elements comprised of other glasses to achieve good correction of chromatic aberration. Since the optical element of the present invention is comprised of a glass of high refractive index, it can be employed in image pickup optical systems, projection optical systems, and the like to render the optical system more compact.
The method of manufacturing the optical element of the present invention will be described next.
The optical element of the present invention can be manufactured by precision press molding the above-described preform of the present invention with a pressing mold.
A desirable form of the method of manufacturing the optical element of the present invention is the method of large-quantity production of optical elements by repeating the step of precision press molding the above-described preform of the present invention in a single pressing mold.
To prevent oxidation of the mold release film provided on the molding surfaces of the pressing mold or the molded surfaces, the step of heating the pressing mold and preform and the precision press molding step are desirably conducted in a non-oxidizing gas atmosphere such as nitrogen gas or a mixed gas of nitrogen gas and hydrogen gas. In a non-oxidizing gas atmosphere, the carbon-containing film coated on the preform surface will remain on the surface of the precision press molded article without oxidizing. This film is eventually to be removed. To relatively easily and completely remove the carbon-containing film, it suffices to heat the precision press molded article in an oxidizing atmosphere, such as air. The oxidation and removal of the carbon-containing film is to be conducted at a temperature at which the precision press molded article will not be deformed by heating. Specifically, this is desirably conducted within a temperature range below the glass transition temperature.
A pressing mold the molding surfaces of which have been processed with high precision into desired shapes in advance is employed in precision press molding. A mold release film can be formed on the molding surfaces to prevent fusion of the glass during pressing. Examples of the mold release film are carbon-containing films, nitride films, and noble metal films. Hydrogenated carbon films, carbon films, and the like are desirable as carbon-containing films.
More specifically, in addition to SiC molds, superhard molds such as WC, molds made of cermets, and the like can be employed as the pressing mold in precision press molding because the glass transition temperature of the optical glass of the present invention is low. As needed, the molding surfaces made of an SiC mold can be coated with a carbon film. As needed, the molding surfaces of a mold made of a superhard material such as WC can be coated with a noble metal film or noble metal alloy film.
The method of manufacturing the optical element comprises the following two forms.
In the first form of the method of manufacturing an optical element by precision press molding (referred to as optical element manufacturing method I), a preform is introduced into the pressing mold and the preform and the pressing mold are heated together. In the second form of the method of manufacturing an optical element by precision press molding (referred to as optical element manufacturing method II), a heated preform is introduced into a preheated pressing mold.
In optical element manufacturing method I, the preform is positioned between a pair of opposing upper and lower molds the molding surfaces of which have been processed into precise shapes, after which both the pressing molds and the preform are heated to a temperature corresponding to a glass viscosity of 105 to 109 dPa·s to soften the preform. The preform is then press molded to precisely transfer the molding surfaces of the pressing molds to the glass. Optical element manufacturing method I is recommended when the focus is on improving molding precision such as surface precision and eccentric precision.
In optical element manufacturing method II, a preform that has been preheated to a temperature corresponding to a glass viscosity of 104 to 108 dPa·s is positioned between a pair of opposing upper and lower molds the molding surfaces of which have been processed into precise shapes and press molded to precisely transfer the molding surfaces of the pressing molds to the glass. Optical element manufacturing method II is recommended when the focus is on increasing productivity.
The pressure and duration of pressing can be suitably determined taking into account the viscosity and the like of the glass. For example, a pressure of about 5 to 15 MPa and a pressing time of 10 to 300 seconds can be employed. Pressing conditions such as the pressing time and pressure can be suitably set to within known ranges in accordance with the shape and dimensions of the molded product.
Subsequently, the pressing mold and precision press molded product are cooled, desirably to a temperature below the strain point, the molds are separated, and the precision press-molded product is removed. To achieve optical characteristics conforming precisely to desired values, it suffices to suitably adjust the annealing conditions of the molded product during cooling, such as the annealing rate.
The optical element of the present invention can be fabricated without a press molding step. For example, a homogeneous glass melt can be cast in a casting mold to form a glass block and annealed to remove strain. Optical characteristics can be adjusted by regulating the annealing conditions to achieve a desired value for the refractive index of the glass. Subsequently, the glass block can be cut or severed to obtain glass pieces, which can then be ground and polished to obtain finished glass elements.
The lens unit of the present invention is assembled into a body of equipment in the form of an optical system comprising optical elements of the present invention, preferably asymmetrical or symmetrical lenses. It can be an interchangeable lens in a single-lens reflex camera, a lens unit built into a compact camera, or the like.
The image pickup device of the present invention is equipped with the above-described optical element of the present invention. Since the optical element of the present invention is comprised of the optical glass having a high refractive index and low dispersion characteristics, a lens with a high dispersion characteristic can be combined with a lens in the form of the optical element of the present invention to provide an image pickup device having a compact image pickup optical system capable of good correction of chromatic aberration. Image sensors such as CCDs and CMOSs can be employed as the image pickup elements constituting the image pickup device.
That is, the image pickup device of the present invention is equipped with at least the above lens unit and image sensors such as CCDs or CMOSs. As needed, a mechanism having a focusing (focus adjusting) function can be provided.
EXAMPLES
The present invention will be described in greater detail below through examples.
Examples
Examples 1 to 33 in Table 3 are mainly examples of Form A. Examples 1 to 44 in Table 4 are mainly examples of Form B. Examples 1 to 28 in Table 5 are mainly examples of Form C. And Examples 1 to 9 in Table 6 are mainly examples of Form D.
Glass starting materials were dispensed in the form of boric acid or boric anhydride, oxides, fluorides, and, as needed, carbonates, nitrates, and the like in a manner calculated to yield optical glasses having the compositions indicated in Tables 3 to 6; charged to a platinum crucible; heated in air, desirably with a platinum cover in place; melted, clarified and homogenized for 1.5 to 3 hours at 1,150 to 1,250° C.; charged to a preheated casting mold; molded; and gradually cooled to obtain glass blocks. No crystal precipitation or striae were observed in the glass. The glass thus obtained was used to measure the various characteristics of glass by the methods outlined in a separate table. The results obtained are given in Tables 3 to 6. The reduction in weight of Example 14 of Table 5, which was of Form C, was 0.61 weight percent. Similarly, the reduction in weight of Example 18 of Table 5 was 1.1 weight percent.
Examples 32 and 33 (Form A) of Table 3 are the glass characteristics obtained by melting for two and a half hours and the various characteristics of other examples given in Tables 3 to 6 are glass characteristics obtained by melting for two hours.








TABLE 3








Example














Example 1
Example 2
Example 3
Example 4
Example 5
Example 6





BO1.5
49.73
49.73
47.80
46.62
45.46
43.48


SiO2
5.52
5.52
7.55
7.36
6.99
8.45


GeO2
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
11.05
11.05
10.06
9.82
9.32
8.45


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00


MgO
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


SrO
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


ZnO
4.42
4.42
5.03
4.91
6.41
7.25


LaO1.5
13.27
13.27
12.58
13.50
13.41
14.49


GdO1.5
12.15
12.15
12.58
13.50
14.57
14.49


YO1.5
0.00
0.00
0.00
0.00
0.00
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
3.31
3.31
3.77
3.68
2.91
2.42


TaO2.5
0.55
0.55
0.63
0.61
0.93
0.97


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
8.84
17.68
5.03
9.82
13.99
14.49


O (Note 3)
137.285
132.865
141.2
138.945
136.36
137.085


F/O(Molar ratio)
0.064
0.133
0.036
0.071
0.103
0.106


Glass transition temperature Tg (° C.)
562
548
578
568
557
558


Liquidus temperature LT (° C.)
1080
1070
1090
1090
1070
1060


Specific gravity
4.66
4.66
4.67
4.61
4.88
4.91


Viscosity at liquidus temperature
2.5
3.0
2.4
2.4
2.9
3.3


(dPa · s)








Refractive index nd
1.76662
1.75392
1.77209
1.77448
1.77356
1.77270


Abbé number νd
49.91
50.84
49.24
49.30
49.40
49.44


nd − (2.25 − 0.01 × νd)
0.016
0.012
0.014
0.017
0.018
0.017


λ80 (nm)
367
364
366
366
362
365


λ70 (nm)
345
343
344
344
340
344


λ5 (nm)
276
275
277
276
278
280


BO1.5 × F/O
3.20
6.62
1.70
3.29
4.66
4.60


Excess B—O—B Bonding:D
11.9
16.3
2.2
0.9
0.0
−6.6


(BBO1.5-(Boxygen-BBO1.5))








SiO2/BO1.5
0.111
0.111
0.158
0.158
0.154
0.194


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
55.25
55.25
55.35
53.98
52.45
51.93


ΣRE
25.41
25.41
25.16
27.00
27.97
28.98


LaO1.5/ΣRE
0.522
0.522
0.500
0.500
0.479
0.500


ΣRE/NWF
0.460
0.460
0.455
0.500
0.533
0.558


2LiO0.5 + ZnO + (F/2)
30.94
35.36
27.67
29.46
32.04
31.40


2LiO0.5/(2LiO0.5 + ZnO)
0.833
0.833
0.800
0.800
0.744
0.700


ZnO + 3ZrO2 + 5TaO2.5
17.10
17.10
19.49
19.00
19.79
19.36


Volatilization peak Tv (° C.) (Note 4)








Weight loss (wt %) (Note 5)



0.41




BO1.5 × F/LaO1.5
16.56
33.13
9.56
16.96
23.71
21.74


ZrO2/(ZrO2 + TaO2.5)
0.86
0.86
0.86
0.86
0.76
0.71


ZrO2 + TaO2.5
3.86
3.86
4.40
4.29
3.84
3.39












Example














Example 7
Example 8
Example 9
Example 10
Example 11
Example 12





BO1.5
42.97
43.22
39.74
41.50
41.42
52.94


SiO2
8.35
8.40
11.54
10.06
7.84
3.53


GeO2
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
5.97
7.20
11.54
10.06
4.48
4.71


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00


MgO
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


SrO
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


ZnO
11.93
7.20
6.41
8.81
13.44
6.47


LaO1.5
14.32
15.31
13.46
13.21
15.68
15.29


GdO1.5
14.32
15.31
13.46
13.21
15.68
12.94


YO1.5
0.00
0.00
0.00
0.00
0.00
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
1.19
2.40
3.21
2.52
0.56
3.53


TaO2.5
0.95
0.96
0.64
0.63
0.90
0.59


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
14.32
19.21
7.69
7.55
22.4
14.12


O (Note 3)
136.625
135.955
139.425
138.68
132.7
139.115


F/O(Molar ratio)
0.105
0.141
0.055
0.054
0.169
0.101


Glass transition temperature Tg (° C.)
562
564
563
559
555
579


Liquidus temperature LT (° C.)
1070
1060
1120
1070
1050
1070


Specific gravity
4.95
4.99
4.75
4.77
5.10
4.87


Viscosity at liquidus temperature
3.0
3.4
1.9
2.9
3.7
3.0


(dPa · s)








Refractive index nd
1.77221
1.77473
1.77021
1.77113
1.77039
1.77960


Abbé number νd
49.31
49.60
48.93
49.09
49.70
49.61


nd − (2.25 − 0.01 × νd)
0.015
0.021
0.010
0.012
0.017
0.026


λ80 (nm)
366
366
363
362
364
366


λ70 (nm)
343
344
342
342
342
344


λ5 (nm)
279
277
277
278
278
275


BO1.5 × F/O
4.50
6.11
2.19
2.26
6.99
5.37


Excess B—O—B Bonding:D
−7.7
−6.3
−20.2
−14.2
−8.4
19.7


(BBO1.5-(Boxygen-BBO1.5))








SiO2/BO1.5
0.194
0.194
0.290
0.242
0.189
0.067


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
51.32
51.62
51.28
51.56
49.26
56.47


ΣRE
28.64
30.62
26.92
26.42
31.36
28.23


LaO1.5/ΣRE
0.500
0.500
0.500
0.500
0.500
0.542


ΣRE/NWF
0.558
0.593
0.525
0.512
0.637
0.500


2LiO0.5 + ZnO + (F/2)
31.03
31.20
33.34
32.70
33.60
22.95


2LiO0.5/(2LiO0.5 + ZnO)
0.500
0.667
0.783
0.695
0.400
0.593


ZnO + 3ZrO2 + 5TaO2.5
20.25
19.20
19.24
19.52
19.62
20.01


Volatilization peak Tv (° C.) (Note 4)








Weight loss (wt %) (Note 5)




1.21



BO1.5 × F/LaO1.5
21.49
27.11
11.35
11.86
29.59
24.44


ZrO2/(ZrO2 + TaO2.5)
0.56
0.71
0.83
0.80
0.38
0.86


ZrO2 + TaO2.5
2.14
3.36
3.85
3.15
1.46
4.12












Example














Example 13
Example 14
Example 15
Example 16
Example 17
Example 18





BO1.5
43.47
43.48
42.46
45.46
45.46
42.71


SiO2
8.45
3.62
8.25
6.99
6.99
8.30


GeO2
0.00
4.83
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
8.45
8.45
2.36
8.16
8.16
2.37


NaO0.5
0.00
0.00
0.00
1.17
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
1.17
0.00


MgO
0.00
0.00
0.00
0.00
0.00
0.00


CaO
0.00
0.00
0.00
0.00
0.00
1.19


SrO
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


ZnO
7.25
7.25
16.51
6.41
6.41
13.05


LaO1.5
12.08
14.49
14.74
13.40
13.40
15.42


GdO1.5
12.08
14.49
14.74
14.57
14.57
15.42


YO1.5
4.83
0.00
0.00
0.00
0.00
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
2.42
2.42
0.00
2.91
2.91
0.59


TaO2.5
0.97
0.97
0.94
0.93
0.93
0.95


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
14.49
14.49
16.51
13.99
13.99
18.98


O (Note 3)
137.085
137.085
136.195
136.35
136.35
136.415


F/O(Molar ratio)
0.106
0.106
0.121
0.103
0.103
0.139


Glass transition temperature Tg (° C.)
560
558
566
554
553
569


Liquidus temperature LT (° C.)
1110
1060
1060
1060
1060
1060


Specific gravity
4.76
5.00
5.04
4.84
4.86
5.06


Viscosity at liquidus temperature
2.0
3.1
3.4
3.2
3.2
3.4


(dPa · s)








Refractive index nd
1.76758
1.78220
1.77393
1.76819
1.77085
1.77450


Abbé number νd
49.61
48.02
49.07
49.42
49.44
49.46


nd − (2.25 − 0.01 × νd)
0.014
0.012
0.015
0.012
0.015
0.019


λ80 (nm)
364
364
368
367
367
367


λ70 (nm)
343
341
346
345
346
345


λ5 (nm)
277
276
276
277
278
276


BO1.5 × F/O
4.59
4.60
5.15
4.66
4.66
5.94


Excess B—O—B Bonding:D
−6.7
−6.6
−8.8
0.0
0.0
−8.3


(BBO1.5-(Boxygen-BBO1.5))








SiO2/BO1.5
0.194
0.083
0.194
0.154
0.154
0.194


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
51.92
51.93
50.71
52.45
52.45
51.01


ΣRE
28.99
28.98
29.48
27.97
27.97
30.84


LaO1.5/ΣRE
0.417
0.500
0.500
0.479
0.479
0.500


ΣRE/NWF
0.558
0.558
0.581
0.533
0.533
0.605


2LiO0.5 + ZnO + (F/2)
31.40
31.40
29.48
29.72
29.72
27.28


2LiO0.5/(2LiO0.5 + ZnO)
0.700
0.700
0.222
0.718
0.718
0.266


ZnO + 3ZrO2 + 5TaO2.5
19.36
19.36
21.21
19.79
19.79
19.57


Volatilization peak Tv (° C.) (Note 4)








Weight loss (wt %) (Note 5)
0.18
0.52






BO1.5 × F/LaO1.5
26.07
21.74
23.78
23.73
23.73
26.29


ZrO2/(ZrO2 + TaO2.5)
0.71
0.71
0.00
0.76
0.76
0.38


ZrO2 + TaO2.5
3.39
3.39
0.94
3.84
3.84
1.54












Example














Example 19
Example 20
Example 21
Example 22
Example 23
Example 24





BO1.5
42.71
44.27
42.34
44.56
43.48
40.76


SiO2
8.30
8.61
9.96
8.66
8.45
7.93


GeO2
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
2.37
9.23
9.34
8.66
8.45
2.27


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00


MgO
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


SrO
0.00
0.00
0.00
0.00
0.00
0.00


BaO
1.19
0.00
0.00
0.00
0.00
0.00


ZnO
13.05
6.15
6.23
7.43
7.25
13.59


LaO1.5
15.42
16.61
14.32
13.61
15.94
19.25


GdO1.5
15.42
11.69
14.32
10.64
10.14
14.72


YO1.5
0.00
0.00
0.00
2.97
2.90
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
0.59
2.46
2.49
2.48
2.42
0.57


TaO2.5
0.95
0.98
1.00
0.99
0.97
0.91


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
18.98
12.3
12.45
14.85
14.49
27.18


O (Note 3)
136.415
138.06
138.545
136.76
137.085
132.505


F/O(Molar ratio)
0.139
0.089
0.09
0.109
0.106
0.205


Glass transition temperature Tg (° C.)
569
561
563
559
562
563


Liquidus temperature LT (° C.)
1060
1120
1080
1050
1070
1070


Specific gravity
5.08
4.79
4.84
4.69
4.76
5.18


Viscosity at liquidus temperature
3.4
1.9
2.7
3.6
2.9
3.0


(dPa · s)








Refractive index nd
1.77379
1.77235
1.77142
1.76321
1.77105
1.77567


Abbé number νd
49.45
49.48
48.48
49.93
49.57
49.66


nd − (2.25 − 0.01 × νd)
0.018
0.017
0.006
0.012
0.017
0.022


λ80 (nm)
368
362
363
364
367
367


λ70 (nm)
347
342
342
343
344
346


λ5 (nm)
277
277
278
278
279
275


BO1.5 × F/O
5.94
3.94
3.80
4.84
4.60
8.36


Excess B—O—B Bonding:D
−8.3
−5.2
−11.5
−3.1
−6.6
−10.2


(BBO1.5-(Boxygen-BBO1.5))








SiO2/BO1.5
0.194
0.194
0.235
0.194
0.194
0.195


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
51.01
52.88
52.30
53.22
51.93
48.69


ΣRE
30.84
28.30
28.64
27.22
28.98
33.97


LaO1.5/ΣRE
0.500
0.587
0.500
0.500
0.550
0.567


ΣRE/NWF
0.605
0.535
0.548
0.512
0.558
0.698


2LiO0.5 + ZnO + (F/2)
27.28
30.76
31.14
32.18
31.40
31.72


2LiO0.5/(2LiO0.5 + ZnO)
0.266
0.750
0.750
0.700
0.700
0.250


ZnO + 3ZrO2 + 5TaO2.5
19.57
18.43
18.70
19.82
19.36
19.85


Volatilization peak Tv (° C.) (Note 4)








Weight loss (wt %) (Note 5)




0.69



BO1.5 × F/LaO1.5
26.29
16.39
18.41
24.31
19.76
28.78


ZrO2/(ZrO2 + TaO2.5)
0.38
0.72
0.71
0.71
0.71
0.39


ZrO2 + TaO2.5
1.54
3.44
3.49
3.47
3.39
1.48












Example














Example 25
Example 26
Example 27
Example 28
Example 29
Example 30





BO1.5
40.76
42.34
42.34
41.57
41.57
41.51


SiO2
7.93
9.96
9.96
9.78
9.78
10.06


GeO2
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
2.27
9.34
9.34
8.56
8.56
10.06


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00


MgO
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


SrO
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


ZnO
13.59
6.23
6.23
7.33
7.33
8.81


LaO1.5
14.72
9.34
19.30
13.21
14.67
11.32


GdO1.5
19.25
19.30
9.34
13.20
11.74
11.32


YO1.5
0.00
0.00
0.00
2.93
2.93
3.77


TiO2
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
0.57
2.49
2.49
2.44
2.44
2.52


TaO2.5
0.91
1.00
1.00
0.98
0.98
0.63


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
27.18
12.45
12.45
14.67
14.67
7.55


O (Note 3)
132.505
138.545
138.545
137.53
137.53
138.68


F/O(Molar ratio)
0.205
0.09
0.09
0.107
0.107
0.054


Glass transition temperature Tg (° C.)
565
567
557
560
559
553


Liquidus temperature LT (° C.)
1090
1100
1100
1070
1070
1080


Specific gravity
5.26
4.94
4.76
4.83
4.80
4.65


Viscosity at liquidus temperature
2.5
2.2
2.2
3.0
3.0
2.7


(dPa · s)








Refractive index nd
1.77441
1.77058
1.77366
1.76989
1.77068
1.76737


Abbé number νd
49.80
49.59
49.34
49.41
49.36
49.36


nd − (2.25 − 0.01 × νd)
0.022
0.016
0.017
0.014
0.014
0.011


λ80 (nm)
368
366
364
364
364
362


λ70 (nm)
347
346
342
344
343
341


λ5 (nm)
277
278
274
276
276
278


BO1.5 × F/O
8.36
3.80
3.80
4.43
4.43
2.26


Excess B—O—B Bonding:D
−10.2
−11.5
−11.5
−12.8
−12.8
−14.2


(BBO1.5-(Boxygen-BBO1.5))








SiO2/BO1.5
0.195
0.235
0.235
0.235
0.235
0.242


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
48.69
52.30
52.30
51.35
51.35
51.57


ΣRE
33.97
28.64
28.64
29.33
29.34
26.41


LaO1.5/ΣRE
0.433
0.326
0.674
0.450
0.500
0.429


ΣRE/NWF
0.698
0.548
0.548
0.571
0.571
0.512


2LiO0.5 + ZnO + (F/2)
31.72
31.14
31.14
31.78
31.78
32.70


2LiO0.5/(2LiO0.5 + ZnO)
0.250
0.750
0.750
0.700
0.700
0.695


ZnO + 3ZrO2 + 5TaO2.5
19.85
18.70
18.70
19.55
19.55
19.52


Volatilization peak Tv (° C.) (Note 4)








Weight loss (wt %) (Note 5)








BO1.5 × F/LaO1.5
37.63
28.22
13.66
23.08
20.79
13.84


ZrO2/(ZrO2 + TaO2.5)
0.39
0.71
0.71
0.71
0.71
0.80


ZrO2 + TaO2.5
1.48
3.49
3.49
3.42
3.42
3.15












Example













Example 31
Example 32
Example 33






BO1.5
41.72
45.51
46.62



SiO2
8.11
7.19
7.36



GeO2
0.00
0.00
0.00



AlO1.5
0.00
0.00
0.00



LiO0.5
4.63
9.58
9.82



NaO0.5
0.00
0.00
0.00



KO0.5
0.00
0.00
0.00



MgO
0.00
0.00
0.00



CaO
0.00
0.00
0.00



SrO
0.00
0.00
0.00



BaO
0.00
0.00
0.00



ZnO
13.90
4.79
4.91



LaO1.5
13.90
14.37
13.49



GdO1.5
12.75
14.37
13.50



YO1.5
3.48
0.00
0.00



TiO2
0.00
0.00
0.00



ZrO2
0.58
2.99
3.07



TaO2.5
0.93
1.20
1.23



NbO2.5
0.00
0.00
0.00



WO3
0.00
0.00
0.00



YbO1.5
0.00
0.00
0.00



CeO2
0.00
0.00
0.00



SnO2
0.00
0.00
0.00



SbO1.5
0.00
0.00
0.00



Total (Note 1)
100.00
100.00
100.00



F (Note 2)
23.17
14.37
9.82



O (Note 3)
132.11
137.13
139.26



F/O(Molar ratio)
0.175
0.105
0.071



Glass transition temperature Tg (° C.)
548
562
566



Liquidus temperature LT (° C.)
1140
1090
1100



Specific gravity
4.93
4.89
4.89



Viscosity at liquidus temperature
1.6
2.5
2.4



(dPa · s)






Refractive index nd
1.76871
1.77470
1.77700



Abbé number νd
49.65
49.34
49.21



nd − (2.25 − 0.01 × νd)
0.015
0.018
0.019



λ80 (nm)
364
364
367



λ70 (nm)
343
342
346



λ5 (nm)
278
277
279



BO1.5 × F/O
7.32
4.77
3.29



Excess B—O—B Bonding:D
−6.9
−0.6
0.6



(BBO1.5-(Boxygen-BBO1.5))






SiO2/BO1.5
0.194
0.158
0.158



NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
49.83
52.70
53.98



ΣRE
30.13
28.74
27.00



LaO1.5/ΣRE
0.461
0.500
0.500



ΣRE/NWF
0.605
0.545
0.500



2LiO0.5 + ZnO + (F/2)
34.75
31.14
29.46



2LiO0.5/(2LiO0.5 + ZnO)
0.400
0.800
0.800



ZnO + 3ZrO2 + 5TaO2.5
20.29
19.76
20.27



Volatilization peak Tv (° C.) (Note 4)






Weight loss (wt %) (Note 5)






BO1.5 × F/LaO1.5
34.77
22.76
16.97



ZrO2/(ZrO2 + TaO2.5)
0.38
0.71
0.71



ZrO2 + TaO2.5
1.51
4.19
4.30





(Note 1) The contents of BO1.5 to SbO1.5 are given as cationic percentages.


(Note 2) F is the relative quantity (in moles) of fluorine ions for the total quantity of cations, denoted as 100.


(Note 3) O is the relative quantity (in moles) of oxygen ions for the total quantity of cations, denoted as 100.


(Note 4) Volatilization peak Tv is the temperature (° C.) of the endothermic peak accompanying change in the discontinuous weight reduction rate of the glass when heated to 1,200° C. at 10° C./min.


(Note 5) The weight reduction was the amount of weight reduction (wt %) when 100 mg of glass was heated from 400° C. to 1,200° C. at 10° C./min.














TABLE 4








Example















Example 1
Example 2
Example 3
Example 4
Example 5
Example 6
Example 7





BO1.5
47.60
42.10
44.56
40.07
36.46
35.11
32.92


SiO2
4.80
6.32
3.96
7.38
10.55
10.16
10.65


GeO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
4.80
5.26
7.92
7.38
8.63
10.16
9.69


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


MgO
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


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


ZnO
11.40
12.63
11.88
8.43
7.67
9.24
9.69


LaO1.5
15.20
15.79
14.85
18.98
18.99
18.29
19.18


GdO1.5
9.50
10.53
9.90
11.28
11.41
10.99
11.53


YO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
2.90
3.16
2.97
2.90
2.64
2.54
2.66


TaO2.5
3.80
4.21
3.96
3.58
3.65
3.51
3.68


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
8.00
8.42
7.92
16.87
15.35
14.78
15.50


O (Note 3)
143.15
143.17
139.61
138.69
140.11
137.69
138.05


F/O(Molar ratio)
0.056
0.059
0.057
0.122
0.110
0.107
0.112


Glass transition temperature
574
570
549
567
562
550
551


Tg (° C.)









Liquidus temperature LT (° C.)
1070
1090
1090
1090
1130
1130
1120


Specific gravity
4.96
5.11
5.02
5.14
5.10
5.08
5.17


Viscosity at liquidus temperature
5.8
4.6
4.0
3.3
2.4
2.3
2.6


(dPa · s)









Refractive index nd
1.80178
1.81460
1.80670
1.80453
1.80188
1.80034
1.80547


Abbé number νd
45.87
44.88
45.24
46.34
46.35
46.21
45.92


nd − (2.25 − 0.01 × νd)
0.010
0.013
0.009
0.018
0.015
0.012
0.015


λ80 (nm)
380
382
379
376
376
373
378


λ70 (nm)
356
356
354
352
352
349
352


λ5 (nm)
285
284
283
282
281
280
281


BO1.5 × F/O
2.67
2.48
2.54
4.89
4.01
3.76
3.69


Excess B—O—B Bonding:D
−0.3
−16.9
−5.9
−18.5
−30.7
−32.4
−39.3


(BBO1.5-(Boxygen-BBO1.5))









SiO2/BO1.5
0.101
0.150
0.089
0.184
0.289
0.289
0.324


NWF (BO1.5 + SiO2 + AlO1.5 +
52.40
48.42
48.52
47.45
47.01
45.27
43.57


GeO2)









ΣRE
24.70
26.32
24.75
30.26
30.40
29.28
30.71


LaO1.5/ΣRE
0.615
0.600
0.600
0.627
0.625
0.625
0.625


ΣRE/NWF
0.471
0.544
0.510
0.638
0.647
0.647
0.705


2LiO0.5 + ZnO + (F/2)
25.00
27.36
31.68
31.62
32.60
36.95
36.82


2LiO0.5/(2LiO0.5 + ZnO)
0.457
0.454
0.571
0.636
0.692
0.687
0.667


ZnO + 3ZrO2 + 5TaO2.5
39.10
43.16
40.59
35.03
33.84
34.41
36.07


Volatilization peak Tv (° C.)
>1200
>1200
1104
1164
1084
1150
1128


(Note 4)









Weight loss (wt %) (Note 5)









BO1.5 × F/LaO1.5
12.53
11.22
11.88
17.81
14.74
14.19
13.30


ZrO2/(ZrO2 + TaO2.5)
0.43
0.43
0.43
0.45
0.42
0.42
0.42


ZrO2 + TaO2.5
6.70
7.37
6.93
6.48
6.29
6.05
6.34












Example














Example 8
Example 9
Example 10
Example 11
Example 12
Example 13





BO1.5
34.34
35.38
49.05
49.59
47.39
46.86


SiO2
11.14
10.24
1.09
1.10
1.10
1.08


GeO2
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
8.35
8.38
3.26
3.29
3.30
3.30


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00


MgO
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


SrO
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


ZnO
9.28
9.31
13.08
13.23
13.22
13.08


LaO1.5
18.84
18.90
15.69
15.21
15.87
15.69


GdO1.5
11.74
11.78
10.47
10.14
10.58
10.46


YO1.5
0.00
0.00
0.00
0.00
0.00
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
2.97
2.56
3.00
3.03
3.03
2.99


TaO2.5
3.34
3.45
4.36
4.41
4.41
4.36


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
1.10
2.18


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
14.85
14.90
17.44
17.64
17.63
17.43


O (Note 3)
139.98
139.37
137.89
137.75
139.40
141.11


F/O(Molar ratio)
0.106
0.107
0.126
0.128
0.126
0.124


Glass transition temperature Tg (° C.)
561
560
569
568
565
565


Liquidus temperature LT (° C.)
1110
1090
1090
1090
1080
1100


Specific gravity
5.13
5.14
5.18
5.15
5.27
5.31


Viscosity at liquidus temperature
3.1
3.9
3.0
2.9
3.3
2.7


(dPa · s)








Refractive index nd
1.80431
1.80417
1.81301
1.81036
1.82374
1.82991


Abbé number νd
46.25
46.27
45.32
45.25
43.52
42.30


nd − (2.25 − 0.01 × νd)
0.017
0.017
0.016
0.013
0.009
0.003


λ80 (nm)
375
375
380
376
389
396


λ70 (nm)
350
350
353
349
364
370


λ5 (nm)
280
280
280
279
330
336


BO1.5 × F/O
3.64
3.79
6.18
6.35
5.97
5.81


Excess B—O—B Bonding:D
−37.0
−33.2
9.3
11.0
2.8
−0.5


(BBO1.5-(Boxygen-BBO1.5))








SiO2/BO1.5
0.324
0.289
0.022
0.022
0.023
0.023


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
45.48
45.62
50.14
50.69
48.49
47.94


ΣRE
30.58
30.68
26.16
25.35
26.45
26.15


LaO1.5/ΣRE
0.616
0.616
0.600
0.600
0.600
0.600


ΣRE/NWF
0.672
0.673
0.522
0.500
0.545
0.545


2LiO0.5 + ZnO + (F/2)
33.40
33.52
28.32
28.63
28.63
28.40


2LiO0.5/(2LiO0.5 + ZnO)
0.643
0.643
0.333
0.332
0.333
0.335


ZnO + 3ZrO2 + 5TaO2.5
34.89
34.24
43.88
44.37
44.36
43.85


Volatilization peak Tv (° C.) (Note 4)
1036
1171
1115
1105
1114
1094


Weight loss (wt %) (Note 5)








BO1.5 × F/LaO1.5
13.53
13.95
27.26
28.76
26.32
26.03


ZrO2/(ZrO2 + TaO2.5)
0.47
0.43
0.41
0.41
0.41
0.41


ZrO2 + TaO2.5
6.31
6.01
7.36
7.44
7.44
7.35












Example














Example 14
Example 15
Example 16
Example 17
Example 18
Example 19





BO1.5
47.37
46.84
48.43
45.57
48.45
47.31


SiO2
1.11
1.09
0.00
2.28
0.00
2.28


GeO2
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
3.30
3.30
3.38
3.43
3.37
3.41


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00


MgO
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


SrO
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


ZnO
13.23
13.08
13.53
13.67
13.86
14.35


LaO1.5
15.87
15.69
16.23
16.41
16.23
16.41


GdO1.5
10.58
10.46
10.82
10.94
10.82
10.94


YO1.5
0.00
0.00
0.00
0.00
0.00
0.00


TiO2
1.10
2.18
0.00
0.00
0.00
0.00


ZrO2
3.03
3.00
3.10
3.14
2.76
2.45


TaO2.5
4.41
4.36
4.51
4.56
4.51
2.85


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
17.64
17.44
18.04
18.23
18.03
18.23


O (Note 3)
138.30
138.94
136.90
137.89
136.58
135.52


F/O(Molar ratio)
0.128
0.126
0.132
0.132
0.132
0.135


Glass transition temperature Tg (° C.)
565
565
562
565
557
549


Liquidus temperature LT (° C.)
1100
1100
1100
1100
1100
1100


Specific gravity
5.21
5.20
5.25
5.25
5.25
5.12


Viscosity at liquidus temperature
2.6
2.7
2.5
2.7
2.5
2.7


(dPa · s)








Refractive index nd
1.82431
1.83253
1.82100
1.81848
1.81804
1.79861


Abbé number νd
43.48
42.05
44.77
44.82
44.90
46.78


nd − (2.25 − 0.01 × νd)
0.009
0.003
0.019
0.017
0.017
0.016


λ80 (nm)
394
407
380
377
377
372


λ70 (nm)
363
370
351
349
349
346


λ5 (nm)
329
335
279
279
278
278


BO1.5 × F/O
6.06
5.90
6.39
6.02
6.40
6.39


Excess B—O—B Bonding:D
3.8
1.6
8.4
−1.2
8.8
6.4


(BBO1.5-(Boxygen-BBO1.5))








SiO2/BO1.5
0.023
0.023
0.000
0.050
0.000
0.048


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
48.48
47.93
48.43
47.85
48.45
49.59


ΣRE
26.45
26.15
27.05
27.35
27.05
27.35


LaO1.5/ΣRE
0.600
0.600
0.600
0.600
0.600
0.600


ΣRE/NWF
0.546
0.546
0.558
0.572
0.558
0.552


2LiO0.5 + ZnO + (F/2)
28.65
28.40
29.31
29.64
29.61
30.29


2LiO0.5/(2LiO0.5 + ZnO)
0.333
0.335
0.333
0.334
0.327
0.322


ZnO + 3ZrO2 + 5TaO2.5
44.37
43.88
45.38
45.89
44.69
35.95


Volatilization peak Tv (° C.) (Note 4)
1121
1043
1157
1140
1036
1176


Weight loss (wt %) (Note 5)








BO1.5 × F/LaO1.5
26.33
26.03
26.92
25.31
26.91
26.28


ZrO2/(ZrO2 + TaO2.5)
0.41
0.41
0.41
0.41
0.38
0.46


ZrO2 + TaO2.5
7.44
7.36
7.61
7.70
7.27
5.30












Example














Example 20
Example 21
Example 22
Example 23
Example 24
Example 25





BO1.5
36.57
35.58
36.82
36.81
36.82
36.82


SiO2
7.41
8.60
8.47
8.47
8.47
8.47


GeO2
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
2.78
3.23
3.17
1.06
3.17
3.17


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00


MgO
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


SrO
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


ZnO
11.67
13.55
13.33
15.45
13.33
13.33


LaO1.5
22.08
19.84
19.52
19.52
25.87
22.70


GdO1.5
14.72
13.23
13.02
13.02
6.67
9.84


YO1.5
0.00
0.00
0.00
0.00
0.00
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
1.99
2.31
2.28
2.28
2.28
2.28


TaO2.5
2.78
3.66
3.39
3.39
3.39
3.39


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
34.26
26.88
23.28
23.28
23.28
23.28


O (Note 3)
131.74
135.67
137.29
138.34
137.29
137.29


F/O(Molar ratio)
0.260
0.198
0.170
0.168
0.170
0.170


Glass transition temperature Tg (° C.)
553
561
558
578
566
568


Liquidus temperature LT (° C.)
1080
1070
1070
1070
1120
1120


Specific gravity
5.39
5.34
5.30
5.34
5.18
5.24


Viscosity at liquidus temperature
1.7
3.4
4.0
4.4
2.3
2.3


(dPa · s)








Refractive index nd
1.79496
1.80384
1.80542
1.80975
1.80677
1.80607


Abbé number νd
47.86
46.36
46.40
46.03
46.26
46.35


nd − (2.25 − 0.01 × νd)
0.024
0.017
0.019
0.020
0.019
0.020


λ80 (nm)
372
375
374
376
377
374


λ70 (nm)
346
350
348
350
351
350


λ5 (nm)
278
279
278
278
278
279


BO1.5 × F/O
9.51
7.04
6.26
6.18
6.26
6.26


Excess B—O—B Bonding:D
−22.0
−28.9
−26.8
−27.9
−26.8
−26.8


(BBO1.5-(Boxygen-BBO1.5))








SiO2/BO1.5
0.203
0.242
0.230
0.230
0.230
0.230


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
43.98
44.18
45.29
45.28
45.29
45.29


ΣRE
36.80
33.07
32.54
32.54
32.54
32.54


LaO1.5/ΣRE
0.600
0.600
0.600
0.600
0.795
0.698


ΣRE/NWF
0.837
0.748
0.719
0.719
0.719
0.718


2LiO0.5 + ZnO + (F/2)
34.36
33.45
31.31
29.21
31.31
31.31


2LiO0.5/(2LiO0.5 + ZnO)
0.323
0.323
0.322
0.121
0.322
0.322


ZnO + 3ZrO2 + 5TaO2.5
31.54
38.78
37.12
39.24
37.12
37.12


Volatilization peak Tv (° C.) (Note 4)
1137
1194
1121
1114
1054
1128


Weight loss (wt %) (Note 5)

0.74
0.61





BO1.5 × F/LaO1.5
28.37
24.10
21.96
21.95
16.57
18.88


ZrO2/(ZrO2 + TaO2.5)
0.42
0.39
0.40
0.40
0.40
0.40


ZrO2 + TaO2.5
4.77
5.97
5.67
5.67
5.67
5.67












Example














Example 26
Example 27
Example 28
Example 29
Example 30
Example 31





BO1.5
36.82
36.82
36.82
36.82
38.32
38.12


SiO2
8.47
8.47
8.47
8.47
8.11
8.07


GeO2
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
3.17
3.17
3.17
3.17
1.01
1.01


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00


MgO
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


SrO
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


ZnO
13.33
13.33
13.33
13.33
16.83
16.74


LaO1.5
16.35
13.17
17.62
15.71
18.70
18.61


GdO1.5
16.19
19.37
11.75
10.48
12.47
12.41


YO1.5
0.00
0.00
3.17
6.35
0.00
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
2.28
2.28
2.28
2.28
3.04
2.52


TaO2.5
3.39
3.39
3.39
3.39
1.52
2.52


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
23.28
23.28
23.28
23.28
22.30
22.19


O (Note 3)
137.29
137.29
137.29
137.29
136.52
137.34


F/O(Molar ratio)
0.170
0.170
0.170
0.170
0.163
0.162


Glass transition temperature Tg (° C.)
572
569
569
569
580
581


Liquidus temperature LT (° C.)
1120
1120
1120
1120
1130
1120


Specific gravity
5.36
5.42
5.22
5.13
5.20
5.25


Viscosity at liquidus temperature
2.3
2.3
2.3
2.3
2.3
2.5


(dPa · s)








Refractive index nd
1.80466
1.80487
1.80155
1.79808
1.79900
1.80284


Abbé number νd
46.49
46.50
46.57
46.75
47.11
46.54


nd − (2.25 − 0.01 × νd)
0.020
0.020
0.017
0.016
0.020
0.018


λ80 (nm)
376
379
379
375
374
375


λ70 (nm)
352
355
350
349
350
350


λ5 (nm)
280
283
280
279
279
279


BO1.5 × F/O
6.26
6.26
6.26
6.26
6.25
6.18


Excess B—O—B Bonding:D
−26.8
−26.8
−26.8
−26.8
−21.6
−23.0


(BBO1.5-(Boxygen-BBO1.5))








SiO2/BO1.5
0.230
0.230
0.230
0.230
0.212
0.212


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
45.29
45.29
45.29
45.29
46.43
46.19


ΣRE
32.54
32.54
32.54
32.54
31.17
31.02


LaO1.5/ΣRE
0.502
0.405
0.542
0.483
0.600
0.600


ΣRE/NWF
0.718
0.719
0.718
0.719
0.671
0.672


2LiO0.5 + ZnO + (F/2)
31.31
31.31
31.31
31.31
30.00
29.85


2LiO0.5/(2LiO0.5 + ZnO)
0.322
0.322
0.322
0.322
0.107
0.108


ZnO + 3ZrO2 + 5TaO2.5
37.12
37.12
37.12
37.12
33.55
36.90


Volatilization peak Tv (° C.) (Note 4)
1061
1148
1084
1106
1024
1020


Weight loss (wt %) (Note 5)








BO1.5 × F/LaO1.5
26.21
32.54
24.32
27.28
22.85
22.73


ZrO2/(ZrO2 + TaO2.5)
0.40
0.40
0.40
0.40
0.67
0.50


ZrO2 + TaO2.5
5.67
5.67
5.67
5.67
4.56
5.04












Example














Example 32
Example 33
Example 34
Example 35
Example 36
Example 37





BO1.5
36.44
42.84
41.57
48.52
48.52
36.66


SiO2
8.38
9.79
8.99
1.08
1.08
8.47


GeO2
0.00
0.00
0.00
2.16
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
2.16
0.00


LiO0.5
0.00
8.57
3.37
3.23
3.23
2.12


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
1.06


MgO
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


SrO
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


ZnO
17.38
0.00
11.24
12.94
12.94
13.33


LaO1.5
19.32
18.36
17.98
14.88
14.88
19.52


GdO1.5
12.88
12.24
12.36
9.92
9.92
13.02


YO1.5
0.00
0.00
0.00
0.00
0.00
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
2.25
3.30
0.00
2.96
2.96
2.34


TaO2.5
3.35
4.90
4.49
4.31
4.31
3.48


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
27.23
20.81
17.98
17.25
17.25
23.28


O (Note 3)
136.36
142.47
141.01
139.09
138.01
137.40


F/O(Molar ratio)
0.200
0.146
0.128
0.124
0.125
0.169


Glass transition temperature Tg (° C.)
588
589
574
568
563
576


Liquidus temperature LT (° C.)
1120
1120
1120
1120
1120
1120


Specific gravity
5.35
5.05
5.18
5.12
5.08
5.28


Viscosity at liquidus temperature
2.2
2.2
2.8
2.2
2.2
2.4


(dPa · s)








Refractive index nd
1.80517
1.79086
1.79454
1.80723
1.80365
1.80163


Abbé number νd
46.12
47.05
46.90
45.07
45.56
46.29


nd − (2.25 − 0.01 × νd)
0.016
0.011
0.014
0.008
0.009
0.015


λ80 (nm)
382
371
373
377
382
376


λ70 (nm)
352
348
349
351
358
350


λ5 (nm)
280
281
280
280
286
280


BO1.5 × F/O
7.29
6.25
5.32
6.02
6.07
6.20


Excess B—O—B Bonding:D
−27.0
−14.0
−16.3
6.5
7.6
−27.4


(BBO1.5-(Boxygen-BBO1.5))








SiO2/BO1.5
0.230
0.229
0.216
0.022
0.022
0.231


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
44.82
52.63
50.56
51.76
51.76
45.13


ΣRE
32.20
30.60
30.34
24.80
24.80
32.54


LaO1.5/ΣRE
0.600
0.600
0.593
0.600
0.600
0.600


ΣRE/NWF
0.718
0.581
0.600
0.479
0.479
0.721


2LiO0.5 + ZnO + (F/2)
30.99
27.54
26.97
28.03
28.03
29.21


2LiO0.5/(2LiO0.5 + ZnO)
0.000
1.000
0.375
0.333
0.333
0.241


ZnO + 3ZrO2 + 5TaO2.5
40.88
34.40
33.69
43.37
43.37
37.75


Volatilization peak Tv (° C.) (Note 4)
1081
1050
1037
1079
1092
1106


Weight loss (wt %) (Note 5)








BO1.5 × F/LaO1.5
25.68
24.28
20.79
28.12
28.12
21.86


ZrO2/(ZrO2 + TaO2.5)
0.40
0.40
0.00
0.41
0.41
0.40


ZrO2 + TaO2.5
5.60
8.20
4.49
7.27
7.27
5.82












Example















Example 38
Example 39
Example 40
Example 41
Example 42
Example 43
Example 44





BO1.5
36.66
36.28
36.28
42.16
47.62
50.51
47.87


SiO2
8.47
8.38
8.38
4.56
4.76
5.05
5.32


GeO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
2.12
3.14
3.14
3.42
4.76
5.05
5.32


NaO0.5
1.06
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


MgO
0.00
1.05
0.00
0.00
0.00
0.00
0.00


CaO
0.00
0.00
1.05
0.00
0.00
0.00
0.00


SrO
0.00
0.00
0.00
2.28
0.00
0.00
0.00


BaO
0.00
0.00
0.00
0.00
0.00
0.00
0.00


ZnO
13.33
13.19
13.19
14.36
11.43
6.06
6.38


LaO1.5
19.52
19.32
19.32
16.41
15.24
16.16
17.02


GdO1.5
13.02
12.88
12.88
10.94
9.52
10.10
10.64


YO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
2.34
2.31
2.31
2.45
2.86
3.03
3.19


TaO2.5
3.48
3.45
3.45
3.42
3.81
4.04
4.26


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
23.28
23.04
23.04
18.23
7.62
8.08
8.51


O (Note 3)
137.40
137.02
137.02
136.07
143.34
145.96
145.75


F/O(Molar ratio)
0.169
0.168
0.168
0.134
0.053
0.055
0.058


Glass transition temperature
574
570
570
556
577
590
587


Tg (° C.)









Liquidus temperature LT (° C.)
1120
1120
1120
1120
1060
1060
1070


Specific gravity
5.29
5.28
5.27
5.16
4.97
4.94
5.04


Viscosity at liquidus temperature
2.4
2.3
2.3
2.4
3.2
3.2
2.9


(dPa · s)









Refractive index nd
1.80256
1.80235
1.80368
1.80108
1.80219
1.79967
1.80904


Abbé number νd
46.32
46.48
46.40
46.07
45.83
46.42
45.89


nd − (2.25 − 0.01 × νd)
0.016
0.017
0.018
0.012
0.010
0.014
0.018


λ80 (nm)
373
387
376
378
373
372
375


λ70 (nm)
349
362
350
351
348
348
348


λ5 (nm)
279
299
279
279
281
282
281


BO1.5 × F/O
6.20
6.10
6.10
5.65
2.53
2.80
2.80


Excess B—O—B Bonding:D
−27.4
−28.2
−28.2
−9.6
−0.5
5.6
−2.1


(BBO1.5-(Boxygen-BBO1.5))









SiO2/BO1.5
0.231
0.231
0.231
0.108
0.100
0.100
0.111


NWF (BO1.5 + SiO2 + AlO1.5 +
45.13
44.66
44.66
46.72
52.38
55.56
53.19


GeO2)









ΣRE
32.54
32.20
32.20
27.35
24.76
26.26
27.66


LaO1.5/ΣRE
0.600
0.600
0.600
0.600
0.616
0.615
0.615


ΣRE/NWF
0.721
0.721
0.721
0.585
0.473
0.473
0.520


2LiO0.5 + ZnO + (F/2)
29.21
30.99
30.99
30.32
24.76
20.20
21.28


2LiO0.5/(2LiO0.5 + ZnO)
0.241
0.323
0.323
0.323
0.454
0.625
0.625


ZnO + 3ZrO2 + 5TaO2.5
37.75
37.37
37.37
38.81
39.06
35.35
37.25


Volatilization peak Tv (° C.)
1059
1027
1104
1046





(Note 4)









Weight loss (wt %) (Note 5)




0.20
0.11
0.07


BO1.5 × F/LaO1.5
21.86
21.63
21.63
23.42
11.91
12.63
11.97


ZrO2/(ZrO2 + TaO2.5)
0.40
0.40
0.40
0.42
0.43
0.43
0.43


ZrO2 + TaO2.5
5.82
5.76
5.76
5.87
6.67
7.07
7.45





(Note 1) The contents of BO1.5 to SbO1.5 are given as cationic percentages.


(Note 2) F is the relative quantity (in moles) of fluorine ions for the total quantity of cations, denoted as 100.


(Note 3) O is the relative quantity (in moles) of oxygen ions for the total quantity of cations, denoted as 100.


(Note 4) Volatilization peak Tv is the temperature (° C.) of the endothermic peak accompanying change in the discontinuous weight reduction rate of the glass when heated to 1,200° C. at 10° C./min.


(Note 5) The weight reduction was the amount of weight reduction (wt %) when 100 mg of glass was heated from 400° C. to 1,200° C. at 10° C./min.





















TABLE 5








Example 1
Example 2
Example 3
Example 4
Example 5
Example 6
Example 7
Example 8





BO1.5
47.36
47.36
47.36
47.35
47.37
47.36
47.36
48.67


SiO2
10.53
10.53
10.53
10.53
8.77
7.02
9.65
9.29


GeO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
14.04
14.04
14.04
14.04
14.04
14.04
14.04
13.72


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00
0.00


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
0.00
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
0.00


ZnO
0.00
0.00
0.00
0.00
0.00
0.00
0.00
0.88


LaO1.5
10.53
17.54
19.02
13.60
14.04
14.04
14.04
13.72


GdO1.5
14.03
7.02
4.07
13.60
14.03
14.03
14.03
13.72


YO1.5
3.51
3.51
4.98
0.00
0.00
0.00
0.00
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
0.00
0.00
0.00
0.88
1.75
3.51
0.00
0.00


TaO2.5
0.00
0.00
0.00
0.00
0.00
0.00
0.88
0.00


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
14.04
14.04
14.04
14.04
14.04
14.04
14.04
14.16


O (Note 3)
134.210
134.210
134.210
134.650
134.20
134.21
134.65
133.41


F/O(Molar ratio)
0.105
0.105
0.105
0.104
0.105
0.105
0.104
0.106


Glass transition temperature
567
558
556
560
558
557
563
555


Tg (° C.)










Liquidus temperature LT (° C.)
1080
1070
1120
1090
1090
1100
1070
1040


Specific gravity(g/cm3)
4.44
4.32
4.12
4.49
4.60
4.66
4.60
4.52


Viscosity at liquidus temperature
1.6
1.8
1.0
1.4
1.4
1.2
1.8
2.4


(dPa · s)










Refractive index nd
1.72358
1.72598
1.72510
1.73004
1.74346
1.75760
1.73636
1.72686


Abbé number νd
54.45
54.18
54.25
53.72
52.69
51.19
52.94
54.41


nd − (2.25 − 0.01 × νd)
0.018
0.018
0.018
0.017
0.020
0.020
0.016
0.021


λ80 (nm)
359
357
361
360
370
373
368
356


λ70 (nm)
340
338
342
341
344
346
345
336


λ5 (nm)
278
261
273
279
275
277
278
276


BO1.5 × F/O
4.97
4.97
4.97
4.92
4.97
4.97
4.93
5.16


Excess B—O—B Bonding:D
7.9
7.9
7.9
74
7.9
7.9
7.4
12.6


(BBO1.5-(Boxygen-BBO1.5))










SiO2/BO1.5
0.222
0.222
0.222
0.222
0.185
0.148
0.204
0.191


NWF (BO1.5 + SiO2 + AlO1.5 +
57.89
57.89
57.89
57.88
56.14
54.38
57.01
57.96


GeO2)










ΣRE
28.07
28.07
28.07
27.20
28.07
28.07
28.07
27.44


LaO1.5/ΣRE
0.375
0.625
0.678
0.500
0.500
0.500
0.500
0.500


ΣRE/NWF
0.485
0.485
0.485
0.470
0.500
0.516
0.492
0.473


2LiO0.5 + ZnO + (F/2)
35.10
35.10
35.10
35.10
35.10
35.10
35.10
35.40


2LiO0.5/(2LiO0.5 + ZnO)
1.000
1.000
1.000
1.000
1.000
1.000
1.000
0.969


ZnO + 3ZrO2 + 5TaO2.5
0.00
0.00
0.00
2.64
5.25
10.53
4.40
0.88


Volatilization peak Tv (° C.)










(Note 4)










Weight loss (wt %) (Note 5)










BO1.5 × F/LaO1.5
31.57
18.95
17.48
24.44
23.69
23.68
23.68
25.12


ZrO2/(ZrO2 + TaO2.5)
N/A
N/A
N/A
1.00
1.00
1.00
0.00
N/A


ZrO2 + TaO2.5
0.00
0.00
0.00
0.88
1.75
3.51
0.88
0.00


















Example 9
Example 10
Example 11
Example 12
Example 13
Example 14
Example 15





BO1.5
60.11
49.56
48.24
48.89
47.41
48.24
46.43


SiO2
0.00
9.46
9.65
9.78
11.21
10.53
10.71


GeO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
8.20
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
14.21
12.61
12.28
12.44
11.21
11.40
14.29


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


MgO
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
1.79


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


ZnO
0.00
0.00
2.63
0.89
3.45
2.63
0.00


LaO1.5
8.74
13.96
13.60
13.78
13.36
13.60
13.39


GdO1.5
8.74
13.96
13.60
13.78
13.36
13.60
13.39


YO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
0.00
0.45
0.00
0.44
0.00
0.00
0.00


TaO2.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
100.00
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
8.74
14.41
17.54
14.22
13.79
14.04
10.71


O (Note 3)
131.42
135.14
132.46
135.12
135.78
135.53
134.82


F/O(Molar ratio)
0.067
0.107
0.132
0.105
0.102
0.104
0.079


Glass transition temperature Tg (° C.)
547
558
553
566
562
565
556


Liquidus temperature LT (° C.)
1040
1050
1040
1040
1050
1040
1100


Specific gravity(g/cm3)
3.86
4.54
4.55
4.54
4.53
4.54
4.46


Viscosity at liquidus temperature
2.0
2.4
2.8
2.8
3.0
3.0
1.4


(dPa · s)









Refractive index nd
1.68084
1.73062
1.72482
1.73085
1.72791
1.72955
1.72912


Abbé number νd
56.60
54.16
54.42
54.06
54.00
54.04
53.82


nd − (2.25 − 0.01 × νd)
−0.003
0.022
0.019
0.021
0.018
0.020
0.017


λ80 (nm)
371
356
354
356
353
354
360


λ70 (nm)
355
336
334
338
336
336
339


λ5 (nm)
298
277
276
277
277
277
274


BO1.5 × F/O
4.03
5.30
6.37
5.13
4.84
5.02
3.67


Excess B—O—B Bonding:D
48.9
13.5
12.3
11.6
6.4
9.2
4.5


(BBO1.5-(Boxygen-BBO1.5))









SiO2/BO1.5
0.000
0.191
0.200
0.200
0.236
0.218
0.231


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
68.31
59.02
57.89
58.67
58.62
58.77
57.14


ΣRE
17.48
27.92
27.20
27.56
26.72
27.20
26.78


LaO1.5/ΣRE
0.500
0.500
0.500
0.500
0.500
0.500
0.500


ΣRE/NWF
0.256
0.473
0.470
0.470
0.456
0.463
0.469


2LiO0.5 + ZnO + (F/2)
32.79
32.43
35.96
32.88
32.77
32.45
33.94


2LiO0.5/(2LiO0.5 + ZnO)
1.000
1.000
0.903
0.965
0.867
0.897
1.000


ZnO + 3ZrO2 + 5TaO2.5
0.00
1.35
2.63
2.21
3.45
2.63
0.00


Volatilization peak Tv (° C.) (Note 4)









Weight loss (wt %) (Note 5)









BO1.5 × F/LaO1.5
30.06
25.58
31.11
25.23
24.47
24.90
18.57


ZrO2/(ZrO2 + TaO2.5)
N/A
1.00
N/A
1.00
N/A
N/A
N/A


ZrO2 + TaO2.5
0.00
0.45
0.00
0.44
0.00
0.00
0.00






Example 16
Example 17
Example 18
Example 19
Example 20
Example 21
Example 22





BO1.5
46.43
46.43
46.52
41.80
61.82
56.03
42.48


SiO2
10.71
10.71
10.08
14.55
4.55
7.25
14.16


GeO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
14.29
14.29
12.40
14.55
7.27
8.70
14.16


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


MgO
0.00
0.00
0.00
0.00
0.00
0.00
0.00


CaO
0.00
0.00
0.00
0.00
3.64
5.80
0.00


SrO
1.79
0.00
0.00
0.00
0.00
0.00
0.00


BaO
0.00
1.79
0.00
0.00
0.00
0.00
0.00


ZnO
0.00
0.00
0.00
0.00
0.00
0.00
0.00


LaO1.5
13.39
13.39
15.50
14.55
12.27
16.91
14.60


GdO1.5
13.39
13.39
15.50
14.55
10.45
4.83
14.60


YO1.5
0.00
0.00
0.00
0.00
0.00
0.48
0.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


TaO2.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


WO3
0.00
0.00
0.00
0.00
0.00
0.00
0.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
10.71
10.71
24.79
14.55
10.91
11.59
10.62


O (Note 3)
134.82
134.82
130.25
135.45
137.73
136.23
137.61


F/O(Molar ratio)
0.079
0.079
0.190
0.107
0.079
0.085
0.077


Glass transition temperature Tg (° C.)
561
557
554
561
599
578
574


Liquidus temperature LT (° C.)
1110
1110
1060
1080
1070
1070
1120


Specific gravity(g/cm3)
4.48
4.50
4.70
4.55
4.17
3.98
4.57


Viscosity at liquidus temperature
1.2
1.2
2.0
1.6
1.6
1.8
1.2


(dPa · s)









Refractive index nd
1.72923
1.72886
1.72964
1.72849
1.70816
1.70373
1.73803


Abbé number νd
53.90
53.75
54.65
53.88
56.25
56.07
53.06


nd − (2.25 − 0.01 × νd)
0.018
0.016
0.026
0.017
0.021
0.014
0.019


λ80 (nm)
361
363
358
357
358
358
364


λ70 (nm)
342
343
339
337
339
341
345


λ5 (nm)
275
277
274
278
278
278
279


BO1.5 × F/O
3.67
3.67
8.84
4.47
4.88
4.76
3.27


Excess B—O—B Bonding:D
4.5
4.5
9.3
−10.1
47.7
31.9
−10.2


(BBO1.5-(Boxygen-BBO1.5))









SiO2/BO1.5
0.231
0.231
0.217
0.348
0.074
0.129
0.333


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
57.14
57.14
56.60
56.35
66.37
63.28
56.64


ΣRE
26.78
26.78
31.00
29.10
22.72
22.22
29.20


LaO1.5/ΣRE
0.500
0.500
0.500
0.500
0.540
0.761
0.500


ΣRE/NWF
0.469
0.469
0.548
0.516
0.342
0.351
0.516


2LiO0.5 + ZnO + (F/2)
33.94
33.94
37.20
36.37
19.99
23.20
33.63


2LiO0.5/(2LiO0.5 + ZnO)
1.000
1.000
1.000
1.000
1.000
1.000
1.000


ZnO + 3ZrO2 + 5TaO2.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00


Volatilization peak Tv (° C.) (Note 4)









Weight loss (wt %) (Note 5)









BO1.5 × F/LaO1.5
18.57
18.57
37.20
20.90
27.48
19.20
15.45


ZrO2/(ZrO2 + TaO2.5)
N/A
N/A
N/A
N/A
N/A
N/A
N/A


ZrO2 + TaO2.5
0.00
0.00
0.00
0.00
0.00
0.00
0.00



















Example 23
Example 24
Example 25
Example 26
Example 27
Example 28






BO1.5
44.84
63.58
51.03
62.06
60.71
63.75



SiO2
10.34
2.89
3.06
2.66
2.60
2.73



GeO2
0.00
0.00
0.00
0.00
0.00
0.00



AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00



LiO0.5
13.79
15.03
12.24
7.09
6.94
7.29



NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00



KO0.5
0.00
0.00
0.00
0.00
0.00
0.00



MgO
5.17
0.00
0.00
0.00
0.00
0.00



CaO
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



BaO
0.00
0.00
0.00
0.00
0.00
0.00



ZnO
0.00
0.00
5.61
2.66
2.60
0.00



LaO1.5
12.93
9.25
13.27
13.56
13.27
13.93



GdO1.5
12.93
6.95
11.22
11.97
11.71
12.30



YO1.5
0.00
0.00
0.00
0.00
0.00
0.00



TiO2
0.00
0.00
0.00
0.00
0.00
0.00



ZrO2
0.00
0.00
3.06
0.00
2.17
0.00



TaO2.5
0.00
0.00
0.51
0.00
0.00
0.00



NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00



WO3
0.00
0.00
0.00
0.00
0.00
0.00



YbO1.5
0.00
2.30
0.00
0.00
0.00
0.00



CeO2
0.00
0.00
0.00
0.00
0.00
0.00



SnO2
0.00
0.00
0.00
0.00
0.00
0.00



SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00



Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00



F (Note 2)
10.34
9.25
20.41
10.64
10.41
10.93



O (Note 3)
133.63
131.79
128.32
137.59
138.94
138.61



F/O(Molar ratio)
0.077
0.070
0.159
0.077
0.075
0.079



Glass transition temperature Tg (° C.)
550
566
519
590
591
604



Liquidus temperature LT (° C.)
1090
1040
1070
1070
1060
1070



Specific gravity(g/cm3)
4.41
4.54
4.61
4.50
4.52
4.46



Viscosity at liquidus temperature
1.4
3.0
3.0
3.0
3.3
3.0



(dPa · s)









Refractive index nd
1.72536
1.68597
1.74343
1.73570
1.74675
1.73115



Abbé number νd
53.93
57.31
51.52
54.17
52.64
54.83



nd − (2.25 − 0.01 × νd)
0.015
0.009
0.009
0.027
0.023
0.029



λ80 (nm)
379
354
358
361
359
358



λ70 (nm)
362
336
338
340
338
337



λ5 (nm)
312
277
265
275
275
275



BO1.5 × F/O
3.45
4.45
8.12
4.80
4.55
5.03



Excess B—O—B Bonding:D
0.9
59.0
24.8
48.6
43.2
52.6



(BBO1.5-(Boxygen-BBO1.5))









SiO2/BO1.5
0.231
0.045
0.060
0.043
0.043
0.043



NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
55.18
66.47
54.09
64.72
63.31
66.48



ΣRE
25.86
18.50
24.49
25.53
24.98
26.23



LaO1.5/ΣRE
0.500
0.500
0.542
0.531
0.531
0.531



ΣRE/NWF
0.469
0.278
0.453
0.395
0.395
0.395



2LiO0.5 + ZnO + (F/2)
32.75
34.68
40.29
22.16
21.68
20.04



2LiO0.5/(2LiO0.5 + ZnO)
1.000
1.000
0.814
0.842
0.842
1.000



ZnO + 3ZrO2 + 5TaO2.5
0.00
0.00
17.34
2.66
9.11
0.00



Volatilization peak Tv (° C.) (Note 4)









Weight loss (wt %) (Note 5)



0.69
0.78
0.71



BO1.5 × F/LaO1.5
17.93
31.79
39.24
24.35
23.81
25.01



ZrO2/(ZrO2 + TaO2.5)
N/A
N/A
0.86
N/A
1.00
N/A



ZrO2 + TaO2.5
0.00
0.00
3.57
0.00
2.17
0.00





(Note 1) The contents of BO1.5 to SbO1.5 are given as cationic percentages.


(Note 2) F is the relative quantity (in moles) of fluorine ions for the total quantity of cations, denoted as 100.


(Note 3) O is the relative quantity (in moles) of oxygen ions for the total quantity of cations, denoted as 100.


(Note 4) Volatilization peak Tv is the temperature (° C.) of the endothermic peak accompanying change in the discontinuous weight reduction rate of the glass when heated to 1,200° C. at 10° C./min.


(Note 5) The weight reduction was the amount of weight reduction (wt %) when 100 mg of glass was heated from 400° C. to 1,200° C. at 10° C./min.














TABLE 6








Example














Example 1
Example 2
Example 3
Example 4
Example 5
Example 6





BO1.5
35.61
34.96
37.00
36.29
33.11
42.00


SiO2
1.87
1.84
1.95
1.91
3.89
0.00


GeO2
0.00
0.00
0.00
0.00
0.00
0.00


AlO1.5
0.00
0.00
0.00
0.00
0.00
0.00


LiO0.5
3.75
3.68
3.89
3.82
3.89
0.00


NaO0.5
0.00
0.00
0.00
0.00
0.00
0.00


KO0.5
0.00
0.00
0.00
0.00
0.00
0.00


MgO
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


SrO
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


ZnO
17.81
17.48
18.50
18.15
18.50
19.00


LaO1.5
20.62
21.16
19.47
20.06
20.45
19.00


GdO1.5
7.97
8.74
6.33
7.16
7.30
6.00


YO1.5
0.00
0.00
0.00
0.00
0.00
1.00


TiO2
0.00
0.00
0.00
0.00
0.00
0.00


ZrO2
2.53
2.48
2.63
2.58
2.63
2.00


TaO2.5
5.15
5.06
5.36
5.25
5.36
4.00


NbO2.5
0.00
0.00
0.00
0.00
0.00
0.00


WO3
4.69
4.60
4.87
4.78
4.87
7.00


YbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


CeO2
0.00
0.00
0.00
0.00
0.00
0.00


SnO2
0.00
0.00
0.00
0.00
0.00
0.00


SbO1.5
0.00
0.00
0.00
0.00
0.00
0.00


Total (Note 1)
100.00
100.00
100.00
100.00
100.00
100.00


F (Note 2)
11.25
14.72
3.89
7.64
7.79
8.00


O (Note 3)
146.11
144.34
149.87
147.95
148.89
152.00


F/O(Molar ratio)
0.077
0.102
0.026
0.052
0.052
0.053


Glass transition temperature Tg (° C.)
562
559
568
564
567
585


Liquidus temperature LT (° C.)
1120
1120
1120
1120
1120
1120


Specific gravity
5.65
5.69
5.53
5.61
5.61
5.61


Viscosity at liquidus temperature
1.6
1.4
2.0
1.8
2.0
1.8


(dPa · s)








Refractive index nd
1.87924
1.87679
1.88262
1.88077
1.88283
1.87398


Abbé number νd
37.96
38.19
37.34
37.70
37.44
36.99


nd − (2.25 − 0.01 × νd)
0.009
0.009
0.006
0.008
0.007
−0.006


λ80 (nm)
443
442
443
448
451
438


λ70 (nm)
386
386
385
385
387
387


λ5 (nm)
345
344
347
347
347
350


BO1.5 × F/O
2.74
3.57
0.96
1.89
1.72
2.23


Excess B—O—B Bonding:D
−39.3
−39.5
−38.9
−39.1
−49.6
−26.0


(BBO1.5-(Boxygen-BBO1.5))








SiO2/BO1.5
0.053
0.053
0.053
0.053
0.117
0.000


NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
37.48
36.80
38.95
38.20
37.00
42.00


ΣRE
28.59
29.90
25.80
27.22
27.75
26.00


LaO1.5/ΣRE
0.721
0.708
0.755
0.737
0.737
0.731


ΣRE/NWF
0.763
0.812
0.662
0.712
0.750
0.619


2LiO0.5 + ZnO + (F/2)
30.93
32.20
28.23
29.61
30.17
23.00


2LiO0.5/(2LiO0.5 + ZnO)
0.296
0.296
0.296
0.296
0.296
0.000


ZnO + 3ZrO2 + 5TaO2.5
51.15
50.22
53.19
52.14
53.19
45.00


Volatilization peak Tv (° C.) (Note 4)








Weight loss (wt %) (Note 5)

0.51






BO1.5 × F/LaO1.5
9.71
12.16
3.7
6.91
6.31
8.84


ZrO2/(ZrO2 + TaO2.5)
0.33
0.33
0.33
0.33
0.33
0.33


ZrO2 + TaO2.5
7.68
7.54
7.99
7.83
7.99
6.00












Example













Example 7
Example 8
Example 9






BO1.5
32.00
38.10
36.29



SiO2
6.00
3.81
1.91



GeO2
0.00
0.00
0.00



AlO1.5
0.00
0.00
0.00



LiO0.5
0.00
3.81
3.82



NaO0.5
0.00
0.00
0.00



KO0.5
0.00
0.00
0.00



MgO
0.00
0.00
0.00



CaO
0.00
0.00
0.00



SrO
0.00
0.00
0.00



BaO
0.00
0.00
0.00



ZnO
21.00
15.24
18.15



LaO1.5
21.50
20.95
20.06



GdO1.5
5.00
7.62
7.16



YO1.5
0.00
0.00
0.00



TiO2
0.50
0.00
0.00



ZrO2
2.50
2.86
2.58



TaO2.5
5.00
5.71
5.25



NbO2.5
0.50
0.00
0.00



WO3
6.00
1.90
4.78



YbO1.5
0.00
0.00
0.00



CeO2
0.00
0.00
0.00



SnO2
0.00
0.00
0.00



SbO1.5
0.00
0.00
0.00



Total (Note 1)
100.00
100.00
100.00



F (Note 2)
8.00
11.43
7.64



O (Note 3)
154.50
144.75
147.95



F/O(Molar ratio)
0.052
0.079
0.052



Glass transition temperature Tg (° C.)
597
567
560



Liquidus temperature LT (° C.)
1120
1100
1110



Specific gravity
5.61
5.44
5.60



Viscosity at liquidus temperature
2.0
2.2
2.0



(dPa · s)






Refractive index nd
1.88583
1.85348
1.87976



Abbé number νd
36.33
40.91
37.67



nd − (2.25 − 0.01 × νd)
−0.001
0.013
0.006



λ80 (nm)
441
405
463



λ70 (nm)
388
372
387



λ5 (nm)
351
336
346



BO1.5 × F/O
1.66
3.01
1.87



Excess B—O—B Bonding:D
−58.5
−30.5
−39.1



(BBO1.5-(Boxygen-BBO1.5))






SiO2/BO1.5
0.188
0.100
0.053



NWF (BO1.5 + SiO2 + AlO1.5 + GeO2)
38.00
41.91
38.20



ΣRE
26.50
28.57
27.22



LaO1.5/ΣRE
0.811
0.733
0.737



ΣRE/NWF
0.697
0.682
0.712



2LiO0.5 + ZnO + (F/2)
25.00
28.57
29.61



2LiO0.5/(2LiO0.5 + ZnO)
0.000
0.333
0.296



ZnO + 3ZrO2 + 5TaO2.5
53.50
52.37
52.14



Volatilization peak Tv (° C.) (Note 4)






Weight loss (wt %) (Note 5)

0.23
0.06



BO1.5 × F/LaO1.5
5.95
10.39
6.91



ZrO2/(ZrO2 + TaO2.5)
0.33
0.33
0.33



ZrO2 + TaO2.5
7.50
8.57
7.83





(Note 1) The contents of BO1.5 to SbO1.5 are given as cationic percentages.


(Note 2) F is the relative quantity (in moles) of fluorine ions for the total quantity of cations, denoted as 100.


(Note 3) O is the relative quantity (in moles) of oxygen ions for the total quantity of cations, denoted as 100.


(Note 4) Volatilization peak Tv is the temperature (° C.) of the endothermic peak accompanying change in the discontinuous weight reduction rate of the glass when heated to 1,200° C. at 10° C./min.


(Note 5) The weight reduction was the amount of weight reduction (wt %) when 100 mg of glass was heated from 400° C. to 1,200° C. at 10° C./min.






The value of BB—(BO—BB) was denoted as D, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO. In Example 32 of Table 3, D is −0.60. In Example 33, D is 0.60. Glass in which D was 22.0 was prepared as a reference sample (reference composition).
Changes in the refractive index nd and the Abbé number νd when the melting time was varied were examined for Examples 32 and 33 in Table 3 and the reference composition. The results are given in FIG. 1.
The numbers recorded near the various plots in FIG. 1 denote melting times in unit of hours. Examples 32 and 33 of Table 3, in which D was small, exhibited smaller changes in refractive index and Abbé number for change in melting time than the reference composition.
FIG. 2 shows the change in refractive index in Examples 32 and 33 of Table 3, with the melting time denoted by the horizontal axis and the refractive index nd denoted by the vertical axis.
FIG. 3 shows the change in specific gravity in Examples 32 and 33 of Table 3, with the melting time denoted by the horizontal axis and the specific gravity denoted by the vertical axis.
FIG. 4 shows the change in the glass transition temperature in Example 32 of Table 3, with the melting time denoted by the horizontal axis and the glass transition temperature Tg denoted by the vertical axis.
From these results, it will be understood that the change in characteristics accompanying change in the melting time was smaller in Examples 32 and 33 of Table 3, which had a lower D than in the reference composition, which had a D of 22.0.
When D increased above 22.0, and when it exceeded 60, the change in characteristics accompanying the change in melting time became extremely large. This meant that in the course of preparing the glass, the variation in the various characteristics of the glass ended up increasing. The main factor behind the variation in characteristics was thought to be volatilization from the glass. With pronounced volatilization, striae tended to form in the molded glass.
Additionally, since the value of D was low in the optical glasses of the examples of the present invention, including Examples 32 and 33 of Table 3, volatilization was suppressed, striae tended not to form, and there was little variation in the various characteristics during large-quantity production.
Keeping D within the above desirable range made it possible to control volatilization of the glass, preventing a decrease in quality due to variation in characteristics and striae.
The optical glasses thus obtained were suitable as glass materials for use in precision press molding.
The various characteristics of the optical glasses were measured by the following methods.
(1) The Refractive Index nd and the Abbé Number νd
The refractive indexes nd, nF, and nc of the glasses obtained by lowering the temperature at a rate of −30° C./hour were measured by the refractive index measuring methods of the Japan Optical Glass Industry Association Standards. The Abbé number νd was computed from these results.
(2) The Liquidus Temperature LT and the Viscosity at Liquidus Temperature
The glass was placed in a furnace that had been heated to a predetermined temperature, kept there for two hours, and cooled. The interior of the glass was then observed by optical microscopy at 100-fold magnification to determine the liquidus temperature based on the presence or absence of crystals.
The viscosity of the glass at the liquidus temperature was measured by the rotating cylinder method based on “JIS Z 8803-1991 ‘Liquid Viscosity—Measurement Methods,’ 8. Viscosity measurement by single cylinder type rotational viscometer.”
(3) The Glass Transition Temperature Tg
The glass transition temperature was measured at a heating rate of 10° C./min with a differential scanning calorimeter (DSC3300) made by Bruker ASX.
(4) Specific Gravity
The specific gravity was measured by Archimedes' method.
(5) λ(lambda) 80, λ70, λ5 (nm)
Plate like glass samples that were 1.0 mm in thickness, had two mutually parallel surfaces, and had been optically polished were employed. Monochromatic light of intensity Iin was made to perpendicularly enter one of the optically polished surfaces, pass through the sample, and exit through the other optically polished surface, at which time the intensity was denoted as Iout. The external transmittance Iout/Iin was then calculated. The external transmittance was measured over a wavelength range of 280 to 700 nm. The wavelength at which the external transmittance was 80 percent was denoted as λ80, that at which the external transmittance was 70 percent as λ70, and that at which the external transmittance was 5 percent as λ5.
(6) The Methods of Measuring Change Over Time


    (i) Refractive index nd
    (ii) Abbé number νd
    (iii) Specific gravity
    (iv) Glass transition temperature Tg


The glass melt was sampled during melting and glass samples were used to measure the various characteristics by the above-described methods. A certain interval of time following the sampling was allowed to elapse, the glass melt was again sampled, and the glass samples were used to measure the various characteristics. The change in various characteristics over time was computed from measured values of the various characteristics obtained by two or more samplings and the sampling time interval.
(7) Weight Reduction
The weight reduction indicates the reduction in weight of fluorine-containing glass as glass components volatize during heating. To quantify the level of weight reduction, equipment measuring the change in weight of a sample accompanying change in temperature, such as TG-DTA measurement and TG-MS measurement, can be employed.
In TG-DTA, for example, a glass sample positioned on a precision scale is heated and the weight of the sample at various temperatures is measured to quantify the change in weight of the glass as the temperature rises.
Specifically, a prescribed weight W (about 100 mg) of glass sample in powder form was packed in a Pt cell 5 mm in diameter and 5 mm in height and heated at a rate of 10° C./min to 1,200° C. with a Rigaku Denki TG-DTA (Thermo Plus TG8120). The amount of weight reduction in the glass, Δ(DELTA)W (mg) was then measured, and the weight reduction was calculated as Weight reduction=ΔW/W×100(%).
Since weight reduction that is unrelated to the volatilization of glass components is sometimes observed due to the elimination of moisture and organic material adhering to the glass over the temperature range of from room temperature to 400° C., the weight reduction of the glass was defined as the weight reduction from 400 to 1,200° C.
(8) Volatilization Peak
The volatilization peak is the temperature of the sharp endothermic peak that appears in the high temperature range as the result of measurement by differential scanning calorimetry, DSC. That is, in the TG-DTA measurement of fluorine-containing glass, at temperatures exceeding 900° C., the rate of weight reduction of glass components with temperature change increases discontinuously, and displacement of heat accompanying the absorption of heat by the glass is sometimes observed. With such change in the weight reduction behavior of the glass, the temperature at which the peak in endothermic behavior is exhibited is defined in the present invention as the volatilization peak temperature Tv of the glass. The endothermic peak at temperature Tv can be measured by differential scanning calorimetry DSC if the range of change in the weight reduction rate is specified in advance by TG-DTA measurement.
Pronounced volatilization occurs at and above Tv. The lower temperature limit of the temperature range at which crystals that have precipitated melt is the liquidus temperature LT. So long as the glass melt is maintained at or above LT, crystallization (devitrification) will not occur. If Tv is higher than LT, the glass melt can be molded at a temperature between LT and Tv. Thus, volatilization can be prevented while preventing devitrification. The greater the temperature differential between LT and Tv, the wider the temperature range over which devitrification and volatilization can be prevented, and the easier it is to stably provide high-quality glass.
As the specific magnitude of the rate of weight reduction with temperature change, for a glass weight reduction of 0.5 percent, for example, the rate of weight reduction with temperature change of the glass is about 1×10−3 wt %/° C. below or equal to temperature Tv, becoming about 3×10−3 wt %/° C. above or equal to temperature Tv. For a glass weight reduction of 2 percent, the rate of weight reduction with temperature change is about 1×10−3 wt %/° C. below or equal to temperature Tv, becoming about 15×10−3 wt %/° C. above or equal to temperature Tv.
When LT≦Tv does not hold true, it does not mean that it is impossible to simultaneously prevent both devitrification and volatilization. Since it takes time for crystals to precipitate when maintaining the glass melt at a temperature somewhat lower than LT, volatilization does not occur. (The lower the temperature that is being maintained, the more rapidly crystal precipitation occurs.) Thus, the desirable range of Tv in Form B (Table 4) contains a temperature range that is lower than LT.
Comparative Examples
The glass of Example 5 described in Patent Document 1 (Japanese Unexamined Patent Publication (KOKAI) No. 2005-170782) was prepared by the method described in Patent Document 1. After maintaining the glass at 1,140° C. for two hours, an optical microscope was used to observe whether or not crystals had precipitated. FIG. 7 shows a microscopic photograph of the glass after it had been maintained at this temperature. As will be clear from FIG. 7, crystals were found on the surface and in the interior of the glass. These results clearly indicate that the liquidus temperature of Example 5 described in Patent Document 1 (Japanese Unexamined Patent Publication (KOKAI) No. 2005-170782) was higher than 1,140° C.
Wet Backwordly Comparison Test
The glass (Form B) of Example 22 in Table 4 and the glasses of Examples 2 and 3 in Patent Document 1 were subjected to a wet backwordly comparison test conducted by the following method. The results (photographs) are given in FIG. 8. As a result, it will be understood that while the glass of the present invention exhibited no wet backwordly, the glasses of Examples 2 and 3 of Patent Document 1 exhibited pronounced wet backwordly as well as high volatility.
Transmittance Curve
FIG. 9 shows transmittance curves that are the results of measurement of the spectral transmittance of samples 10 mm in thickness of the following glasses that were reproduced:

    (1) Example 31 (YbO1.5=0 percent) described in Patent Document 3 (WO2004/054937);
    (2) Example 5 (YbO1.5=0 percent) of Patent Document 1 (Japanese Unexamined Patent Publication (KOKAI) No. 2005-170782);
    (3) Example 34 (YbO1.5=6.11 percent);
    (4) Example 3 (YbO1.5=1 percent);
    (5) Example 2 (YbO1.5=0.98 percent).


The glasses of (1) and (2) above that did not contain YbO1.5, described in Patent Documents 1 and 3, had high transmittance over a wavelength range of 900 to 1,000 nm. However, the glasses of (4) and (5), which contained slight amounts of YbO1.5, exhibited transmittance of less than 20 percent over the same wavelength range because of strong absorbance by Yb. Almost no light of the above wavelength passed through the glass of (3). Thus, glasses containing more than 0.5 percent of YbO1.5 are not suitable as materials for optical elements constituting image pickup optical systems in which high transmittance in the infrared range is desirable.
The various above glasses were then ground and polished to prepare precision press-molding preforms. It was possible for the shape of the preforms to be close to the shape of the optical element to be fabricated, spherical, or some other shape.
The entire surface of the preforms thus obtained was coated with a carbon film as necessary. The preforms were heated and precision press molded in a pressing mold to fabricate aspherical lenses such as convex meniscus lenses, concave meniscus lenses, biconvex lenses, biconcave lenses, plano-convex lenses, and plano-concave lenses. Following precision press molding, the molded products were centered as needed to finish the lenses. An antireflective film was also coated as needed on the surfaces of the lenses obtained.
Instead of a SiC mold, it was also possible to conduct precision press molding with a WC mold or a cermet mold. A mold release film in the form of a carbon film could also be coated on the molding surfaces of a SiC mold. A noble metal film, such as platinum, or a noble metal alloy film could also be coated on the molding surfaces of a WC mold.
Due to the low glass transition temperature of the optical glass, it was possible to lower the precision press molding temperature. Thus, good precision press molding could be conducted even without using a mold with extremely good heat resistance such as a SiC mold.
Next, the interchangeable lenses of a single-lens reflex camera and the image pickup optical system of a compact camera that incorporated the various above-described aspherical lenses were fabricated.
Further, the CCDs or CMOSs of the image pickup optical system of a compact camera were assembled to fabricate an image pickup optical system unit, which was built into a compact camera.
INDUSTRIAL APPLICABILITY
The present invention is useful in fields relating to optical glass.

## Claims

1. An optical glass comprising,
denoted as cationic percentages:


















BO1.5
20 to 70
percent;



LaO1.5
6 to 30
percent;



GdO1.5
4 to 25
percent;



SiO2
0 to 20
percent;



LiO0.5
0 to 20
percent;



ZnO
0 to 20
percent;



ZrO2
0 to 4.5
percent;



TaO2.5
0 to 7
percent;



YbO1.5
0 to 0.5
percent;



GeO2
0 to 5
percent;



YO1.5
0.5 to 10
percent;









as well as O and F,
with the F/O molar ratio of the F content to the O content being 0.01 to 0.30;
the combined sum of the ZnO content, three times the ZrO2 content, and five times the TaO2.5 content (ZnO+3ZrO2+5TaO2.5) being 40 percent or less;
the combined sum of twice the LiO0.5 content, the ZnO content, and 1⁄2 the F content (2LiO0.5+ZnO+(F/2)) when the total quantity of cations is denoted as 100 being 20 percent or greater;
the value of BB—(BO—BB) falling within a range of −60 to +20, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO;
the refractive index nd being 1.75 to 1.81;
the Abbé number νd being 48 to 52; and
the glass transition temperature Tg being 590° C. or lower.

2. The optical glass according to claim 1, wherein the refractive index nd and the Abbé number νd of the optical glass satisfy equation (1) below


nd−(2.25−0.01×νd)≧−0.01  (1).

3. An optical glass comprising,
denoted as cationic percentages:


















BO1.5
20 to 70
percent;



LaO1.5
6 to 30
percent;



GdO1.5
4 to 25
percent;



SiO2
0 to 20
percent;



LiO0.5
0 to 20
percent;



ZnO
0 to 25
percent;



ZrO2
8
percent or less;



TaO2.5
7
percent or less;



YbO1.5
0 to 3
percent;



GeO2
0 to 5
percent;









as well as O and F,
with the F/O molar ratio of the F content to the O content being 0.01 to 0.30;
the ratio of the ZrO2 content to the combined content of ZrO2 and TaO2.5 (ZrO2/(ZrO2+TaO2.5)) being 0 to 0.7;
the combined sum of ZrO2 and TaO2.5 (ZrO2+TaO2.5) being 3 to 10;
the combined sum of twice the LiO0.5 content, the ZnO content, and 1⁄2 the F content (2LiO0.5+ZnO+(F/2)) when the total quantity of cations is denoted as 100 being 20 percent or greater;
the value of BB—(BO—BB) falling within a range of −60 to +20, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO;
the refractive index nd being 1.802 to 1.835; and
the Abbé number νd being 42 to 48.

4. The optical glass according to claim 3, wherein the refractive index nd and the Abbé number νd of the optical glass satisfy equation (2) below


nd−(2.25−0.01×νd)≧−0.01  (2).

5. An optical glass comprising,
denoted as cationic percentages:


















BO1.5
20 to 70
percent;



LaO1.5
6 to 30
percent;



GdO1.5
4 to 25
percent;



SiO2
0 to 20
percent;



LiO0.5
0 to 20
percent;



ZnO
0 to 15
percent;



ZrO2
5
percent or less;



TaO2.5
3
percent or less;



YbO1.5
0 to 3
percent;



GeO2
0 to 5
percent;









as well as O and F,
with the F/O molar ratio of the F content to the O content being 0.01 to 0.30;
the combined sum of the ZnO content, three times the ZrO2 content, and five times the TaO2.5 content (ZnO+3ZrO2+5TaO2.5) being 15 percent or less;
the combined sum of twice the LiO0.5 content, the ZnO content, and 1⁄2 the F content (2LiO0.5+ZnO+(F/2)) when the total quantity of cations is denoted as 100 being 20 percent or greater;
the value of BB—(BO—BB) falling within a range of −60 to +60, with the value BB being 1.5 times the content of BO1.5 denoted as a cationic percentage, the total quantity of all cations in the glass being denoted as 100, and the molar ratio of the total oxygen content relative to this total quantity being denoted as BO;
the refractive index nd being 1.675 to 1.745; and
the Abbé number νd being 51 to 58.

6. The optical glass according to claim 5, wherein the refractive index nd and the Abbé number νd of the optical glass satisfy equation (3) below


nd−(2.25−0.01×νd)≧−0.01  (3).

7. A preform for precision press molding that is comprised of an optical glass according to claim 1.

8. An optical element that is comprised of an optical glass according to claim 1.

9. A method of manufacturing an optical element comprises heating and precision press molding a preform according to claim 7 with a pressing mold.

10. A lens unit being equipped with an optical element according to claim 8.

11. An image pickup device being equipped with a lens unit of according to claim 10.