JP2017160118A - Glass, glass material for press molding, optical element blank, and optical element - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a glass that has an Abbe number νd of 39.5-41.5, satisfies the relation of nd≥2.0927-0.0058×νd, and can contribute to the weight saving of optical elements.SOLUTION: The present invention provides an oxide glass in which: in terms of cation%, the total content of B, Si, La, Y, Gd, Yb, Nb, Ti, Ta, W, Zr, Zn, Mg, Ca, Sr, Ba, Li, Na, K, Al, and Biis 90% or more, the total content of La, Y, Gdand Ybis 28-45, the content of Yis 1-20%, the Abbe number νd is 39.5-41.5, and the refractive index nd satisfies the above relation for the Abbe number νd.SELECTED DRAWING: None

Description

  The present invention relates to glass, a glass material for press molding, an optical element blank, and an optical element.

  A lens made of high refractive index and low dispersion glass can be made a cemented lens in combination with a lens made of ultra-low dispersion glass, etc., thereby making it possible to make the optical system compact while correcting chromatic aberration. Therefore, the high refractive index and low dispersion glass occupies a very important position as an optical element constituting a projection optical system such as an imaging optical system or a projector. Such high refractive index low dispersion glass is described in, for example, Patent Documents 1 to 20.

JP 2007-063071 A JP 2007-230835 A JP 2007-249112 A JP 2007-261826 A JP 2003-267748 A JP 2009-203083 A JP 2011-230992 A JP 2012-025638 A JP 54-090218 A Japanese Patent Laid-Open No. 56-160340 JP 2001-348244 A JP 2008-001551 A Special table 2013-536791 gazette WO10 / 053214 JP 2012-180278 A JP 2012-236754 A JP 2014-084235 A JP 2014-062025 A JP 2014-062026 A JP 2011-93780 A

  For glass for optical elements, an optical property map (also called an Abbe chart) is widely used to show the distribution of optical properties. The optical characteristic map has an Abbe number νd on the horizontal axis and a refractive index nd on the vertical axis. The Abbe number νd increases from the right side to the left side of the horizontal axis, and the refractive index increases from the lower side to the upper side of the vertical axis. It is created to increase accordingly. In the following description, the refractive index and Abbe number refer to the refractive index nd with respect to helium d-line (wavelength 587.56 nm) and the Abbe number νd with respect to helium d-line (wavelength 587.56 nm), unless otherwise specified.

In the optical property map, the optical properties of the high refractive index low dispersion glass (high nd high νd glass) increase so that the refractive index increases as the Abbe number decreases, and the refractive index decreases as the Abbe number increases. Distribution is generally shown. This is considered to be due to the following reasons.
Many high-refractive index low-dispersion glasses contain rare earth oxides such as boron oxide and lanthanum oxide. In such a glass, in order to increase the refractive index without reducing the Abbe number, the content of the rare earth oxide is increased. However, when the rare earth oxide content is increased in the conventional high refractive index and low dispersion glass, the thermal stability of the glass is lowered, and the glass tends to be devitrified in the process of producing the glass. Therefore, it has been difficult to increase both the Abbe number and the refractive index of the conventional high refractive low dispersion glass while suppressing the devitrification of the glass to be used as an optical element material. This point is considered to be the reason why the conventional high refractive index and low dispersion glass shows such a distribution in the optical property map.

On the other hand, in the design of optical systems, glass with a high refractive index and a large Abbe number (low dispersion) is a material for optical elements that is extremely effective for correcting chromatic aberration, increasing the functionality of optical systems, and making them more compact. is there. Therefore, it is very meaningful to set a straight line that rises to the right on the optical property map, and to provide glass that has a higher refractive index than this straight line and the straight line (located on the left side of the straight line on the map). Big.
From the above points, the Abbe number νd is 39.5 to 41.5, and with respect to this Abbe number, the glass whose refractive index nd is equal to or larger than the value obtained by 2.0927−0.0058 × νd, that is, nd ≧ 2 Glass satisfying the relationship of 0.0927−0.0058 × νd is a high refractive index and low dispersion glass useful in an optical system.

By the way, it is desirable to reduce the weight of optical elements constituting a projection optical system such as an imaging optical system or a projector. This is because reducing the weight of the optical element leads to a reduction in the weight of the imaging optical system and projection optical system incorporating the optical element. For example, when a heavy optical element is incorporated in an autofocus camera, power consumption when driving autofocus increases, and the battery is quickly consumed. On the other hand, if the optical element is reduced in weight, the power consumption when driving the autofocus can be reduced and the battery life can be extended.
However, the present inventor has an Abbe number νd in the range of 39.5 to 41.5 among the glasses described in Patent Documents 1 to 20, and a relationship of nd ≧ 2.0927−0.0058 × νd. It is considered that an optical element manufactured using a high refractive index and low dispersion glass satisfying the above condition tends to be heavy. This is because the specific gravity of the glass tends to increase in the composition adjustment described in Patent Documents 1 to 20 for high refractive index and low dispersion.

  One embodiment of the present invention provides a glass that has an Abbe number νd of 39.5 to 41.5, satisfies a relationship of nd ≧ 2.0927−0.0058 × νd, and can contribute to weight reduction of an optical element. The purpose is to do.

One embodiment of the present invention provides:
In terms of cation%, B ³⁺ , Si ⁴⁺ , La ³⁺ , Y ³⁺ , Gd ³⁺ , Yb ³⁺ , Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ , W ⁶⁺ , Zr ⁴⁺ , Zn ²⁺ , Mg ²⁺ , Ca ²⁺ , Sr ²⁺ , Ba ²⁺ , Li ⁺ , Na ⁺ , K ⁺ , Al ³⁺ , and Bi ³⁺ are 90% or more,
Abbe number νd is in the range of 39.5-41.5,
Refractive index nd is expressed by the following formula (1) with respect to Abbe number νd:
nd ≧ 2.0927−0.0058 × νd (1)
And the total D of the values obtained by multiplying the content of each cation component by the coefficient described in Table 1 with respect to the refractive index nd is the following formula (B):
D ≦ 6.224 × nd−6.8042 (B)
A glass that is an oxide glass,
About.

The glass is at ^{cationic%, B 3+, Si 4+, La} 3+, Y 3+, Gd 3+, Yb 3+, Nb 5+, Ti 4+, Ta 5+, W 6+, Zr 4+, Zn 2+, Mg 2+, Ca The total content of ²⁺ , Sr ²⁺ , Ba ²⁺ , Li ⁺ , Na ⁺ , K ⁺ , Al ³⁺ , and Bi ³⁺ (hereinafter referred to as these cation components “main cation components”) is 90% or more. The present inventor has paid attention to the fact that the influence of the main cation component on the specific gravity of the glass is different in the intensive study to achieve the above object. As a result of repeated trial and error, the coefficients shown in Table 1 were determined for each of the main cation components. By adjusting the composition so that the total D calculated using these coefficients satisfies the formula (B), nd ≧ 2.0927−0.0058 × when the Abbe number νd is in the range of 39.5 to 41.5. It is possible to provide a glass that can contribute to lowering the specific gravity of the high refractive index and low dispersion glass satisfying the relationship of νd, that is, reducing the weight of the optical element.

  According to one embodiment of the present invention, glass that has optical characteristics useful in an optical system and can contribute to weight reduction of an optical element can be provided. Furthermore, according to one embodiment of the present invention, it is possible to provide a glass material for press molding, an optical element blank, and an optical element made of the glass.

FIG. 1 shows the specific gravity of each glass of Example 1 and each glass of Comparative Examples 1 to 4 on the horizontal axis, and the vertical axis represents the sum D of values obtained by multiplying the content of each cationic component by the coefficient shown in Table 1. It is a graph taken in FIG. 2 is a graph in which the Abbe number νd of each glass of Example 1 and each glass of Comparative Examples 1 to 4 is taken on the horizontal axis, and the value A calculated by the formula (A) described later is taken on the vertical axis. .

[Glass]
The glass according to one embodiment of the present invention includes, in terms of cation%, B ³⁺ , Si ⁴⁺ , La ³⁺ , Y ³⁺ , Gd ³⁺ , Yb ³⁺ , Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ , W ⁶⁺ , Zr ⁴⁺ , Zn The total content of ²⁺ , Mg ²⁺ , Ca ²⁺ , Sr ²⁺ , Ba ²⁺ , Li ⁺ , Na ⁺ , K ⁺ , Al ³⁺ , and Bi ³⁺ is 90% or more, and the Abbe number νd is 39.5 to 41.41. 5 and the refractive index nd satisfies the above formula (1) with respect to the Abbe number νd, and the cation components listed in Table 1 below are listed in Table 1 in the content of each cation component. Is the oxide glass that satisfies the above formula (B) with respect to the refractive index nd.

  Hereinafter, the detail of the said glass is demonstrated.

  The glass composition in the present invention can be quantified by a method such as ICP-AES (Inductively Coupled Plasma-Atomic Emission Spectrometry). The analysis value obtained by ICP-AES may include a measurement error of about ± 5% of the analysis value. Further, in the present specification and the present invention, that the content of the constituent component is 0% or does not contain or is not introduced means that the constituent component is substantially not contained, and the content of the constituent component is an impurity level. It means less than or equal to.

In the present invention, the glass composition is expressed in terms of cation% with respect to the cation component. As is well known, the cation% is a percentage in which the total content of all cation components contained in the glass is 100%.
Hereinafter, unless otherwise specified, the content of the cation component and the total content (total content) of the plurality of types of cation components are expressed in cation%. Furthermore, in the cation% display, the ratio of the contents of cation components (including the total content of plural kinds of cation components) is referred to as a cation ratio.
Below, regarding a numerical range, a (more) preferable lower limit and a (more) preferable upper limit may be shown and described in a table | surface. In the table, the numerical value described below is more preferable, and the numerical value described most downward is most preferable. In addition, unless otherwise specified, the (more) preferred lower limit means that it is (more) preferred to be greater than or equal to the stated value, and the (more) preferred upper limit is less than the stated value. (More) It is preferable. The numerical value range can be defined by arbitrarily combining the numerical values described in the (more) preferable lower limit column and the (more) preferable upper limit column in the table.

<Glass composition>
The glass is B ³⁺ , Si ⁴⁺ , La ³⁺ , Y ³⁺ , Gd ³⁺ , Yb ³⁺ , Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ , W ⁶⁺ , Zr ⁴⁺ , Zn ²⁺ , Mg ²⁺ , Ca ²⁺ , ar ²⁺ The total content of ²⁺ , Li ⁺ , Na ⁺ , K ⁺ , Al3 ⁺ , and Bi3 ⁺ (main cation component) is 90% or more. In the glass, the cation component contained may be only the main cation component (that is, the total content of the main cation components is 100%), and includes one or more other cation components in addition to the main cation component. Also good. The preferable lower limit of the total content of the main cation components is as shown in the following table.

The glass composition of the above glass is the following formula (B) with respect to the refractive index nd, the total D of the values obtained by multiplying the content of each cation component by the coefficient shown in Table 1 for the various cation components of the main cation component. :
D ≦ 6.224 × nd−6.8042 (B)
It is adjusted to meet. As a result, the weight reduction of the high refractive index low dispersion glass satisfying the above-mentioned expression (1) with respect to the Abbe number νd in which the Abbe number νd is in the range of 39.5 to 41.5. Can do. This point was newly found as a result of intensive studies by the present inventors. The total D is as follows in detail. The unit of the following content is cation%.
D = B ³⁺ content × 0.032
+ Si ⁴⁺ content × 0.029
+ La ³⁺ content × 0.066
+ Y ³⁺ content × 0.053
+ Gd ³⁺ content × 0.093
+ Yb ³⁺ content × 0.094
+ Nb ⁵ + content × 0.049
+ Ti ⁴⁺ content × 0.045
+ Ta ⁵⁺ content × 0.104
+ W ⁶⁺ content × 0.111
+ Zr ⁴⁺ content × 0.080
+ Zn ²⁺ content × 0.051
+ Mg ²⁺ content × 0.030
+ Ca ²⁺ content × 0.024
+ Sr ²⁺ content × 0.043
+ Ba ²⁺ content × 0.055
+ Li ⁺ content x 0.031
+ Na ⁺ content × 0.021
+ K ⁺ content x 0.012
+ Al ³⁺ content × 0.034
+ Bi ³⁺ content × 0.090

The above formula (B) is preferably the following formula (B-1), more preferably the following formula (B-2), still more preferably the following formula (B-3), still more preferably the following ( B-4), more preferably the following formula (B-5), still more preferably the following formula (B-6), and still more preferably the following formula (B-7). More preferably, it is the following formula (B-8), and still more preferably the following formula (B-9).
D ≦ 6.224 × nd−6.8142 (B-1)
D ≦ 6.224 × nd−6.8242 (B-2)
D ≦ 6.242 × nd−6.8342 (B-3)
D ≦ 6.242 × nd−6.8442 (B-4)
D ≦ 6.242 × nd−6.8542 (B-5)
D ≦ 6.242 × nd−6.8642 (B-6)
D ≦ 6.242 × nd−6.8742 (B-7)
D ≦ 6.242 × nd−6.8842 (B-8)
D ≦ 6.242 × nd−6.8894 (B-9)

  The glass composition of the said glass should just be what the total content of a main cation component is 90% or more, and satisfy | fills (B) Formula, and is not contained in the said glass in a main cation component ( That is, the content may be 0%). The preferred range of the content of each cation component will be further described later. However, the present invention is not limited to the following preferred ranges.

B ³⁺ and Si ⁴⁺ are glass network forming components. When the total content of B ³⁺ and Si ⁴⁺ (B ³⁺ + Si ⁴⁺ ) is 43% or more, the thermal stability of the glass is improved, and crystallization of the glass during production can be suppressed. On the other hand, when the total content of B ³⁺ and Si ⁴⁺ is 65% or less, a decrease in the refractive index nd can be suppressed, which is preferable in producing a glass having the above-described optical characteristics. Therefore, the total content of B ³⁺ and Si ⁴⁺ in the glass is preferably in the range of 43 to 65%. The more preferable lower limit and the more preferable upper limit of the total content of B ³⁺ and Si ⁴⁺ are as shown in the following table.

La ³⁺ , Y ³⁺ , Gd ³⁺ and Yb ³⁺ are components having a function of increasing the refractive index while suppressing a decrease in the Abbe number νd. These components also have the function of improving the chemical durability and weather resistance of the glass and increasing the glass transition temperature.
When the total content of La ³⁺ , Y ³⁺ , Gd ³⁺ and Yb ³⁺ (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ ) is 25% or more, the decrease in the refractive index nd can be suppressed. It is preferable when producing glass having Furthermore, it is possible to suppress a decrease in chemical durability and weather resistance of the glass. Note that when the glass transition temperature is lowered, the glass is likely to be damaged when mechanically processing (cutting, cutting, grinding, polishing, etc.) the glass (decreasing machinability), but La ³⁺ , Y ³⁺ , Gd ^Since the fall of glass transition temperature can be suppressed as the total content of ³⁺ and Yb ³⁺ is 25% or more, machinability can also be improved. On the other hand, if the total content of each component of La ³⁺ , Y ³⁺ , Gd ³⁺ and Yb ³⁺ is 50% or less, the thermal stability of the glass can be improved. It is also possible to reduce the amount of raw material remaining when the glass is melted. Moreover, it is preferable also from suppressing the raise of specific gravity. Therefore, in the glass, the total content of La ³⁺ , Y ³⁺ , Gd ³⁺ and Yb ³⁺ is preferably in the range of 25 to 50%. More preferable lower limit and more preferable upper limit of the total content of La ³⁺ , Y ³⁺ , Gd ³⁺ and Yb ³⁺ are shown in the following table.

Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ and W ⁶⁺ are components having a function of increasing the refractive index, and also have a function of improving the thermal stability of the glass by containing an appropriate amount. If the total content of Ti ⁴⁺ , Nb ⁵⁺ , Ta ⁵⁺ and W ⁶⁺ (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ ) is 3% or more, the above optical characteristics can be achieved while maintaining thermal stability. preferable. On the other hand, if the total content of Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ and W ⁶⁺ is 12% or less, a decrease in thermal stability and a decrease in Abbe number νd can be suppressed. Thus, in the ^glass, Nb ^5+, Ti 4+, the total content of ^{Ta 5+,} and ^{W 6+,} is preferably in the range 3 to 12%. The more preferable lower limit and the more preferable upper limit of the total content of Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ and W ⁶⁺ are shown in the following table.

Zr ⁴⁺ is a component having a function of increasing the refractive index, and also has a function of improving the thermal stability of the glass by containing an appropriate amount. Zr ⁴⁺ also has a function of making the glass difficult to break during mechanical processing by increasing the glass transition temperature. In order to obtain these effects satisfactorily, in the above glass, it is preferable that the content of Zr ⁴⁺ is 2% or more. On the other hand, if the content of Zr ⁴⁺ is 8% or less, the thermal stability of the glass can be improved, so that crystallization during glass production and generation of unmelted glass during glass melting can be suppressed. . Therefore, the Zr ⁴⁺ content in the glass is preferably in the range of 2 to 8%. The more preferable lower limit and the more preferable upper limit of the Zr ⁴⁺ content are shown in the following table.

In order to realize optical characteristics in which the Abbe number νd is 39.5 to 41.5 and the refractive index nd and Abbe number νd satisfy the relationship of the above formula (1), in the glass, Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ And the cation ratio of Zr ⁴⁺ content to the total content of W ⁶⁺ {Zr ⁴⁺ content / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} is preferably in the range of 0.48 to 2.20. It is preferable that the cation ratio is in the range of 0.48 to 2.20 from the viewpoint of suppressing a decrease in glass transition temperature (improvement of machinability). Moreover, it is preferable that the said cation ratio is 0.48 or more from a viewpoint of the improvement of thermal stability and low dispersion | distribution of glass. On the other hand, it is preferable that the cation ratio is 2.20 or less from the viewpoint of improving the meltability and suppressing crystallization. More preferable lower limits and more preferable upper limits of the cation ratio {Zr ⁴⁺ content / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} are shown in the following table.

In order to improve the thermal stability of the glass, in order to realize optical characteristics in which the Abbe number νd is 39.5 to 41.5 and the refractive index nd and Abbe number νd satisfy the relationship of the above formula (1), In glass, the cation ratio of the total content of B ³⁺ and Si ⁴⁺ to the total content of La ³⁺ , Y ³⁺ , Gd ³⁺ and Yb ³⁺ {(B ³⁺ + Si ⁴⁺ ) / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ ) } Is preferably 0.70 to 1.75. If the cation ratio ((B ³⁺ + Si ⁴⁺ ) / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ )) is 0.70 or more, it is possible to improve the thermal stability of the glass, thereby suppressing devitrification of the glass. can do. Moreover, it is preferable also when suppressing the increase in specific gravity of glass. On the other hand, the cation ratio {(B ³⁺ + Si ⁴⁺ ) / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ )} is preferably 1.75 or less from the viewpoint of realizing the above optical characteristics. More preferable lower limits and more preferable upper limits of the cation ratio {(B ³⁺ + Si ⁴⁺ ) / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ )} are shown in the following table.

In order to improve the thermal stability of the glass and suppress the decrease in the refractive index nd and realize the optical characteristics described above, the glass has a B content relative to the total content of Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ and W ^6+. The cation ratio {(B ³⁺ + Si ⁴⁺ ) / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} of the total content of ³⁺ and Si ⁴⁺ is preferably 9.00 or less.
The cation ratio {(B ³⁺ + Si ⁴⁺ ) / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} is set to 5.00 or more in order to improve the thermal stability of the glass while suppressing the decrease of the Abbe number νd. It is preferable. Furthermore, the cation ratio {(B ³⁺ + Si ⁴⁺ ) / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} is preferably 5.00 or more from the viewpoint of reducing the specific gravity.
More preferable lower limit and more preferable upper limit of the cation ratio {(B ³⁺ + Si ⁴⁺ ) / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} are shown in the following table.

From the viewpoint of reducing the specific gravity of the glass while improving the thermal stability of the glass and suppressing crystallization of the glass, a cation having a W ⁶⁺ content relative to the total content of Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ and W ⁶⁺ The ratio {W ⁶⁺ / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} is preferably 0.50 or less. The cation ratio {W ⁶⁺ / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} is preferably 0.50 or less from the viewpoint of increasing the refractive index of the glass and reducing coloration. More preferable lower limits and more preferable upper limits of the cation ratio {W ⁶⁺ / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} are shown in the following table.

In order to improve the thermal stability of the glass and suppress the crystallization of the glass while realizing the optical characteristics described above, in the glass, Zn with respect to the total content of La ³⁺ , Y ³⁺ , Gd ³⁺ and Yb ³⁺ The cation ratio of ²⁺ content {Zn ²⁺ / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ )} is preferably less than 0.20. In addition, the cation ratio {Zn ²⁺ / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ )} is less than 0.20, which suppresses a decrease in glass transition temperature (improves machinability by this) and improves chemical durability. From the viewpoint of this, it is preferable. The cation ratio {Zn ²⁺ / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ )} is preferably 0% or more and more preferably more than 0% from the viewpoint of improving the meltability. The preferable lower limit and the preferable upper limit of the cation ratio {Zn ²⁺ / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ )} are shown in the following table.

Among the rare earth elements La, Y, Gd, and Yb, Gd belongs to a heavy rare earth element, and is a component that is required to reduce the content in glass from the viewpoint of stable supply of glass. Gd is also a component that has a large atomic weight and increases the specific gravity of the glass.
Yb also belongs to heavy rare earth elements and has a large atomic weight. Yb has absorption in the near infrared region. On the other hand, it is desirable that interchangeable lenses for single-lens reflex cameras and surveillance camera lenses have high light transmittance in the near infrared region. Therefore, in order to obtain glass useful for the production of these lenses, it is desirable to reduce the Yb content.
On the other hand, La and Y do not adversely affect the light transmittance in the near-infrared region, and by distributing an appropriate amount to the total content of rare earth elements, the specific gravity is improved while improving the thermal stability. It is a component useful for suppressing the increase in the refractive index and providing a high refractive index and low dispersion glass.

Therefore, in the glass, the ^{La 3+ is,} La ^3+, Y 3+, the ^{La 3+} content of the cation ratio to the total content of ^{Gd 3+} and ^{Yb 3+ {La 3+ / (La} 3+ + Y 3+ + Gd 3+ + Yb 3+)}, A range of 0.50 to 0.95 is preferable. More preferable lower limits and more preferable upper limits of the cation ratio {La ³⁺ / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ )} are shown in the following table.

^Also, the ^{Y 3+,} La ^3+, Y 3+, the content of the cation ratio of ^{Y 3+} to the total content of ^{Gd 3+} and ^{Yb 3+} a ^{{Y 3+ / (La 3+ +} Y 3+ + Gd 3+ + Yb 3+)} 0.10 It is preferable to be in a range of ˜0.50. More preferable lower limits and more preferable upper limits of the cation ratio {Y ³⁺ / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ )} are shown in the following table.

Gd ³⁺ is a component whose content in the glass should be reduced from the viewpoint of stable glass supply, as described above. In the above glass, the cation ratio {Gd ³⁺ of the content of Gd ³⁺ to the total content of La ³⁺ , Y ³⁺ , Gd ³⁺ and Yb ³⁺ from the viewpoint of stably supplying the high refractive index and low dispersion glass having the optical properties described above. / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ )} is preferably 0.10 or less. Satisfying the cation ratio may contribute to lowering the specific gravity of the glass. More preferable lower limits and more preferable upper limits of the cation ratio {Gd ³⁺ / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ )} are shown in the following table.

La ^{3+, Y} 3+, the total content of ^{Gd 3+} and ^{Yb 3+,} and ^{La 3+} content for this total ^{content, Y 3+} content, the cation ratio of ^{Gd 3+} content is as described above. The preferable lower limit and preferable upper limit of the content of each component of La ³⁺ , Y ³⁺ , Gd ³⁺ , Yb ³⁺ are shown in the following table. In addition, about ^{Y3 +} content, the lower limit shown to the following table | surface is preferable also from a viewpoint of the thermal stability of glass, and a meltability improvement.

Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ and W ⁶⁺ contain an appropriate amount, thereby increasing the refractive index and improving the thermal stability of the glass. However, Ta ⁵⁺ has a function of increasing the refractive index, but is an extremely expensive component. Therefore, it is not preferable to use Ta ⁵⁺ positively from the viewpoint of stable supply of glass. On the other hand, when the content of Ta ⁵⁺ is large, the raw material tends to remain unmelted when the glass is melted. Moreover, the specific gravity of glass increases. Thus, Ta ⁵⁺ is a component whose content should be reduced. Therefore, it is not preferable to use Ta ⁵⁺ positively. For ta ^5+, while improving the thermal stability of the glass, in order to reduce the amount of high refractive index and low dispersion of the ^{Ta, Nb 5+, Ti 4+,} Ta 5+ to the total content of ^{Ta 5+} and ^{W 6+} The cation ratio {Ta ⁵⁺ / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} is preferably 0.2 or less. The preferable lower limit and the more preferable upper limit of the cation ratio {Ta ⁵⁺ / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} are shown in the following table.

As for Nb ⁵⁺ , the content of Gd ³⁺ and Ta ⁵⁺ is reduced in order to enable stable supply of glass, and preferably the content of Yb ³⁺ together with Gd ³⁺ and Ta ⁵⁺ is reduced while being reduced. to provide a high-refractivity low-dispersion glass having excellent ^{stability, Nb 5+, Ti 4+, Ta} 5+, in consideration of the above effects of ^{W 6+, Nb 5+, Ti 4+} , total content of ^{Ta 5+} and ^{W 6+} The cation ratio {Nb ⁵⁺ / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} of the content of Nb ^{5+ to} the amount is preferably 0.2 or more. Nb ⁵⁺ is a component that tends to increase the refractive index without increasing the specific gravity as compared with Ta ⁵ and W ⁶⁺ . Therefore, in order to suppress the increase in specific gravity, it is preferable to increase the cation ratio {Nb ⁵⁺ / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )}. More preferable lower limits and preferable upper limits of the cation ratio {Nb ⁵⁺ / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} are shown in the following table.

Further, from the viewpoint of preventing high dispersion and coloring, the cation ratio of Ti ⁴⁺ content to the total content of Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ and W ⁶⁺ {Ti ⁴⁺ / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} Is preferably 0.6 or less. The preferable lower limit and the more preferable upper limit of the cation ratio {Ti ⁴⁺ / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} are shown in the following table.

La ³⁺ with respect to the total content of Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ and W ⁶⁺ (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ ) in suppressing the decrease in Abbe number νd while maintaining the thermal stability of the glass, Y ^3+, the lower limit of the total content of ^{Gd 3+} and ^{Yb 3+ (La 3+ + Y 3+} + Gd 3+ + Yb 3+) cation ratio of ^{{(La 3+ + Y 3+ +} Gd 3+ + Yb 3+) / (Nb 5+ + Ti 4+ + Ta 5+ + W 6+)} Is preferably a lower limit value shown in the following table.
On the other hand, the upper limit of the cation ratio {(La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ ) / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} is maintained in order to maintain the thermal stability of the glass while suppressing the decrease in the refractive index. The upper limit value shown in the following table is preferable.

  The glass composition of the glass will be further described below.

The total content of B ³⁺ and Si ⁴⁺ , which are glass network forming components, is as described above. Regarding B ³⁺ and Si ⁴⁺ , B ³⁺ is more excellent in improving the ^meltability than Si ^4+, but is likely to volatilize during melting. On the other hand, Si ⁴⁺ has the function of improving the chemical durability, weather resistance, and machinability of glass, and increasing the viscosity of glass during melting.
In general, in a high refractive index low dispersion glass containing rare earth elements such as B ³⁺ and La ³⁺ , the viscosity of the glass at the time of melting is low. However, if the viscosity of the glass at the time of melting is low, crystallization tends to occur. Crystallization during glass production is more stable when crystallized than when it is in an amorphous state (amorphous state), and occurs when ions constituting the glass move in the glass and are arranged so as to have a crystal structure. Therefore, by adjusting the content ratio of each component of B ³⁺ and Si ⁴⁺ so as to increase the viscosity at the time of melting, it becomes difficult to arrange the above ions so as to have a crystal structure, and the crystallization of the glass Furthermore, it can suppress and can further improve the devitrification resistance of glass.
From the above viewpoint, the preferred lower limit and the preferred upper limit of the cation ratio {B ³⁺ / (B ³⁺ + Si ⁴⁺ )} of the B ³⁺ content to the total content of B ³⁺ and Si ⁴⁺ are as shown in the following table. It is preferable to make it more than the lower limit shown in the following table from the viewpoint of improving the meltability of the glass. Moreover, it is preferable to make it below the upper limit shown in the following table, when raising the viscosity of the glass at the time of melting. Furthermore, the upper limit shown in the following table is set to reduce the glass composition variation due to volatilization during melting and the optical property variation due to the volatilization, and to improve the chemical durability, weather resistance and machinability of the glass. It is also preferable from the viewpoint of one or more improvements.

For each of B ³⁺ content and Si ⁴⁺ content, preferred lower and preferred upper limits for improving the devitrification resistance, meltability, moldability, chemical durability, weather resistance, machinability, etc. of the glass, Shown in the table below.

Zn ²⁺ has a function of promoting melting of a glass raw material when melting glass, that is, a function of improving meltability. It also has functions of adjusting the refractive index nd and Abbe number νd and lowering the glass transition temperature. A value obtained by dividing the content of Zn ²⁺ by the total content of B ³⁺ and Si ⁴⁺ , that is, the cation ratio {Zn ²⁺ / (B ³⁺ + Si ⁴⁺ )} From the viewpoints of improvement of stability, suppression of lowering of glass transition temperature (improvement of machinability by this), and reduction of specific gravity of glass, it is preferably 0.15 or less. In the above glass, since Zn is an optional component that may or may not be contained, the cation ratio {Zn ²⁺ / (B ³⁺ + Si ⁴⁺ )} is preferably 0 or more. It is more preferable to contain Zn and make the cation ratio {Zn ²⁺ / (B ³⁺ + Si ⁴⁺ )} greater than 0 in order to improve the thickness and easily produce a homogeneous glass. More preferable lower limits and more preferable upper limits of the cation ratio {Zn ²⁺ / (B ³⁺ + Si ⁴⁺ )} are shown in the following table.

From the viewpoint of improving the meltability, thermal stability, moldability, machinability, etc. of the glass and realizing the optical properties described above, the preferred lower limit and preferred upper limit of the Zn ²⁺ content are as shown in the following table. .

Sum of Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ and W ⁶⁺ from the viewpoint of further improvement of the thermal stability of glass, suppression of lowering of glass transition temperature (improvement of machinability), and improvement of chemical durability The cation ratio of the Zn ²⁺ content to the content {Zn ²⁺ / (Ti ⁴⁺ + Nb ⁵⁺ + Ta ⁵⁺ + W ⁶⁺ )} is preferably 1.0 or less. On the other hand, since Zn is an optional component, the lower limit of the cation ratio {Zn ²⁺ / (Nb ⁵⁺ + Ti ⁴⁺ + Ta ⁵⁺ + W ⁶⁺ )} is preferably 0, but it is more preferably more than 0 from the viewpoint of improving the meltability. preferable. Considering the above points, more preferable lower limits and more preferable upper limits of the cation ratio {Zn ²⁺ / (Ti ⁴⁺ + Nb ⁵⁺ + Ta ⁵⁺ + W ⁶⁺ )} are as shown in the following table.

^{Nb 5+, Ti 4+, Ta 5+} , the ^{W 6+,} in consideration of the above-described action and ^{effect, Nb 5+, Ti 4+, Ta} 5+, the preferred range of the content of each component of ^{W 6+,} shown in the following Table.

  Next, optional components other than the components described above will be described.

Since Li ⁺ has a strong effect of lowering the glass transition temperature, the machinability tends to decrease as the content increases. Also, chemical durability and weather resistance tend to decrease. Therefore, the Li ⁺ content is preferably 5% or less. The preferable lower limit and the more preferable upper limit of the content of Li ⁺ are shown in the following table. The content of Li ⁺ may be 0%.

Na ⁺ , K ⁺ , Rb ⁺ , and Cs ⁺ all have a function of improving the meltability of the glass. However, as the content of these increases, the thermal stability, chemical durability, and weather resistance of the glass are increased. The machinability tends to decrease. Therefore, it is preferable that the lower limit and the upper limit of each content of Na ⁺ , K ⁺ , Rb ⁺ , and Cs ⁺ are as shown in the following table.

In order to improve the meltability of the glass while maintaining the thermal stability, chemical durability, weather resistance and machinability of the glass, the total content of Li ⁺ , Na ⁺ and K ⁺ (Li ⁺ + Na ⁺ The preferred lower limit and the preferred upper limit of + K ⁺ are as shown in the following table.

Mg ²⁺ , Ca ²⁺ , Sr ²⁺ and Ba ²⁺ are all components having a function of improving the meltability of the glass. However, if the content of these components is increased, the thermal stability of the glass is lowered and a tendency to devitrification is exhibited. Therefore, the content of each of these components is preferably not less than the lower limit shown below, and preferably not more than the upper limit.

Moreover, from the viewpoint of maintaining the thermal stability of the glass, the total content of Mg ²⁺ , Ca ²⁺ , Sr ²⁺ and Ba ²⁺ (Mg ²⁺ + Ca ²⁺ + Sr ²⁺ + Ba ²⁺ ) should be at least the lower limit shown in the following table. Is preferable, and the upper limit is preferably set.

Al ³⁺ is a component having a function of improving the chemical durability and weather resistance of glass. However, when the content of Al ³⁺ increases, a tendency of decreasing the refractive index nd, a tendency of decreasing the thermal stability of the glass, and a tendency of decreasing the meltability may be observed. Considering the above points, the Al ³⁺ content is preferably not less than the lower limit shown in the following table, and preferably not more than the upper limit.

Ga ³⁺ , In ³⁺ , Sc ³⁺ , and Hf ⁴⁺ all have a function of increasing the refractive index nd. However, these components are expensive and are not essential components for obtaining the optical glass. Accordingly, the contents of Ga ³⁺ , In ³⁺ , Sc ³⁺ , and Hf ⁴⁺ are preferably set to the lower limit shown in the following table, and preferably set to the upper limit or lower.

Lu ³⁺ has a function of increasing the refractive index nd, but is also a component that increases the specific gravity of the glass. Moreover, since Lu is a heavy rare earth element like Gd and Yb, it is preferable to reduce the content of Lu. From the above points, the preferred lower limit and the preferred upper limit of the Lu ³⁺ content are as shown in the following table.

Ge ⁴⁺ has a function of increasing the refractive index nd, but is a prominent and expensive component among commonly used glass components. From the viewpoint of reducing the manufacturing cost of glass, the preferred lower limit and preferred upper limit of the Ge ⁴⁺ content are as shown in the following table.

Bi ³⁺ is a component that increases the refractive index nd and decreases the Abbe number νd. It is also a component that tends to increase specific gravity and coloring. The preferred lower and preferred upper limits for the Bi ³⁺ content are as shown in the following table for producing a glass having the above-described optical properties and low coloration and low specific gravity.

  In order to obtain the various functions and effects described above satisfactorily, the total content (total content) of the cation components described above is preferably more than 95%, more than 98%. More preferably, more than 99% is still more preferable, and more than 99.5% is still more preferable.

Among the cation components other than the cation components described above, P ⁵⁺ is a component that lowers the refractive index nd and is a component that lowers the thermal stability of the glass. May improve thermal stability. The preferred lower limit and preferred upper limit of the P ⁵⁺ content are as shown in the following table for producing a glass having the above-described optical characteristics and excellent thermal stability.

Te ⁴⁺ is a component that increases the refractive index nd, but since it is a toxic component, it is preferable to reduce the Te ⁴⁺ content. The preferable lower limit and preferable upper limit of the Te ⁴⁺ content are as shown in the following table.

  In addition, it is also preferable that the content of (more) a preferred lower limit or 0% in each of the above tables is 0%. The same applies to the total content of a plurality of components.

The inventors of the present invention have paid attention to the fact that the influence of each cation component on the dispersion (Abbe number) of the glass is considered to be different in the various cation components described above. As a result of further investigations, the present inventors have prescribed a coefficient that takes into consideration the influence on the dispersion of the glass for each cationic component, and the value A calculated by the following formula (A) is 8.5000 to 11.000. It is preferable to adjust the composition so as to be in the range in order to realize optical characteristics in which the Abbe number νd is 39.5 to 41.5 and the refractive index nd and Abbe number νd satisfy the relationship of the above formula (1). I came to think.
A = 0.01 × Si ^{4 +} content + 0.01 × B ^{3 +} content + 0.05 × La ^{3 +} content + 0.07 × Y ^{3 +} content + 0.07 × Yb ^{3 +} content + 0.085 × Zn 2 ⁺ content + 0.3 × Zr ^{4 +} content + 0.5 × Ta ⁵ + content + 0.8 × Nb ⁵ + content + 0.9 × W ⁵ + content + 0.95 × Ti ^{4 +} content (A)

  The more preferable lower limit and the more preferable upper limit of the value A calculated by the above formula (A) are as shown in the following table.

Of the various cation components described above, Nb ⁵⁺ , Ti ⁴⁺ and Gd ³⁺ have the effect of increasing the refractive index and Nb ⁵⁺ and Ti ⁴⁺ have the effect of increasing the specific gravity compared to Gd ^3+. It is a small component. Therefore, balancing the total content of Nb ⁵⁺ and Ti ⁴⁺ with the content of Gd ³⁺ is preferable in order to increase the refractive index while suppressing an increase in specific gravity. From this point, it is preferable that the value C calculated by the following formula (C) is −1,000 or more in the glass composition of the cation% display. Further, from the viewpoint of high refractive index and low dispersion, the value C calculated by the following formula (C) is preferably 6.720 or less.
C = 0.567 × (Nb ⁵ + content + Ti ^{4 +} content) −1.000 × Gd ^{3 +} content (C)

The more preferable lower limit and the more preferable upper limit of the value C calculated by the formula (C) are as shown in the following table.

Pb, As, Cd, Tl, Be, and Se each have toxicity. Therefore, it is preferable not to contain these elements, that is, not to introduce these elements into the glass as glass components.
U, Th, and Ra are all radioactive elements. Therefore, it is preferable not to contain these elements, that is, not to introduce these elements into the glass as glass components.
V, Cr, Mn, Fe, Co, Ni, Cu, Pr, Nd, Pm, Sm, Eu, Tb, Dy, Ho, Er, Tm, and Ce increase the coloration of the glass and become a source of fluorescence. The element contained in the glass for optical elements is not preferable. Therefore, it is preferable not to contain these elements, that is, not to introduce these elements into the glass as glass components.

Sb and Sn are arbitrarily addable elements that function as fining agents.
The addition amount of Sb is converted into _Sb 2 _{O 3,} when the total content of glass components other than _Sb 2 _{O 3} is 100 mass%, preferably in the range of 0 to 0.11 wt%, The range is more preferably 0.01 to 0.08% by mass, and still more preferably 0.02 to 0.05% by mass.
The addition amount of Sn is preferably in the range of 0 to 0.5% by mass when converted to SnO ₂ and the total content of glass components other than SnO ₂ is 100% by mass. A range of 2% by mass is more preferable, and a range of 0% by mass is even more preferable.

  The cationic component has been described above. Next, the anion component will be described.

Since the glass is an oxide glass, it contains O ²⁻ as an anion component. The preferable lower limit of the O ²⁻ content is as shown in the following table.

Examples of the anion component other than O ²⁻ include F ⁻ , Cl ⁻ , Br ⁻ and I ⁻ . However, all of F ⁻ , Cl ⁻ , Br ⁻ and I ⁻ are easily volatilized during melting of the glass. Due to volatilization of these components, the characteristics of the glass fluctuate and the homogeneity of the glass tends to decrease, or the melting equipment tends to be consumed significantly. Therefore, it is preferable to suppress the total content of F ⁻ , Cl ⁻ , Br ⁻ and I ⁻ to an amount obtained by subtracting the content of O ²⁻ from 100 anion%.
As well known, the anion% is a percentage with the total content of all anion components contained in the glass being 100%.

<Glass characteristics>
(Optical properties of glass)
The glass has a Abbe number νd in the range of 39.5 to 41.5, and a refractive index nd satisfies the following formula (1) with respect to the Abbe number νd.
nd ≧ 2.0927−0.0058 × vd (1)
Glass having an Abbe number νd of 39.5 or more is effective for correcting chromatic aberration as a material of an optical element. On the other hand, when the Abbe number νd is larger than 41.5, unless the refractive index is lowered, the thermal stability of the glass is remarkably lowered, and the glass tends to be devitrified in the process of producing the glass. The preferable lower limit and the preferable upper limit of the Abbe number νd are shown in the following table.

In the glass, the refractive index nd satisfies the formula (1) with respect to the Abbe number νd. A glass whose Abbe number νd is in the range of 39.5 to 41.5 and whose refractive index nd satisfies the formula (1) is a glass having high utility value in designing an optical system.
The upper limit of the refractive index nd is naturally determined by the glass composition. In order to improve the thermal stability and obtain a glass that is not easily devitrified, the refractive index nd preferably satisfies the following formula (2).
nd ≦ 2.1270−0.0058 × vd (2)
The preferable lower limit and the more preferable upper limit of the refractive index nd with respect to the Abbe number νd are shown in the following table.

  Further, the refractive index nd is preferably not less than the lower limit shown in the following table, and preferably not more than the upper limit.

(Partial dispersion characteristics)
From the viewpoint of correcting chromatic aberration, the glass is preferably a glass having a small partial dispersion ratio when the Abbe number νd is fixed.
Here, the partial dispersion ratios Pg and F are expressed as (ng−nF) / (nF−nc) using the refractive indexes ng, nF and nc in the g-line, F-line and c-line.
From the viewpoint of providing a glass suitable for higher-order chromatic aberration correction, the preferred lower limit and preferred upper limit of the partial dispersion ratio Pg, f of the glass are as shown in the following table.

(Glass-transition temperature)
Although the glass transition temperature of the said glass is not specifically limited, Preferably it is 640 degreeC or more. By setting the glass transition temperature to 640 ° C. or higher, it is possible to make the glass difficult to break when mechanically processing the glass, such as cutting, cutting, grinding, and polishing. Moreover, since it is not necessary to contain a large amount of components such as Li and Zn that have a strong function of lowering the glass transition temperature, even if the content of Gd and Ta is reduced, the content of Yb is also reduced. However, it becomes easy to improve thermal stability.
On the other hand, if the glass transition temperature is too high, the glass must be annealed at a high temperature, and the annealing furnace is significantly consumed. Further, when glass is molded, it must be molded at a high temperature, and the consumption of the mold used for molding becomes significant.
The preferable lower limit and the preferable upper limit of the glass transition temperature are as shown in the following table in order to improve the machinability and reduce the burden on the annealing furnace and the mold.

(Specific gravity of glass)
In the optical element (lens) constituting the optical system, the refractive power is determined by the refractive index of the glass constituting the lens and the curvature of the optical functional surface of the lens (the surface on which light to be controlled is incident and emitted). If the curvature of the optical function surface is increased, the thickness of the lens also increases. As a result, the lens becomes heavy. On the other hand, if a glass having a high refractive index is used, a large refractive power can be obtained without increasing the curvature of the optical function surface.
As described above, if the refractive index can be increased while suppressing an increase in the specific gravity of the glass, it is possible to reduce the weight of the optical element having a certain refractive power.
Regarding the contribution of the refractive index nd to the refractive power, by taking the ratio of the specific gravity d of the glass to the value obtained by subtracting 1 which is the refractive index in the vacuum (nd-1) from the refractive index nd of the glass, It can be used as an index for reducing the weight of the element. That is, by using d / (nd-1) as an index for reducing the weight of the optical element and reducing this value, it is possible to reduce the weight of the lens.
When the total D satisfies the above formula (B) with respect to the refractive index nd, the glass can be reduced in specific gravity while being a high refractive index and low dispersion glass. Therefore, d / (nd-1) of the glass can be, for example, 5.70 or less. However, if d / (nd-1) is excessively decreased, the thermal stability of the glass tends to decrease. Therefore, d / (nd-1) is preferably set to 5.00 or more. More preferable lower limit and more preferable upper limit of d / (nd-1) are shown in the following table.

  Further, preferred lower limits and preferred upper limits of the specific gravity d of the glass are shown in the following table. Setting the specific gravity d below the upper limit shown in the following table is preferable from the viewpoint of reducing the weight of the optical element made of this glass. Moreover, it is preferable to make specific gravity more than the lower limit shown in the following table | surface in order to improve the thermal stability of glass more.

(Liquid phase temperature)
One indicator of the thermal stability of glass is the liquidus temperature. In order to suppress crystallization and devitrification during glass production, the liquidus temperature LT is preferably 1350 ° C. or lower, more preferably 1330 ° C. or lower, still more preferably 1300 ° C. or lower, 1250 It is still more preferable that it is below ℃. The lower limit of the liquidus temperature LT is 1100 ° C. or more as an example, but is preferably not low and is not particularly limited.

  The glass according to one embodiment of the present invention described above has a large refractive index nd and Abbe number νd, and is useful as a glass material for optical elements. Furthermore, it is possible to homogenize and lower the specific gravity of the glass by adjusting the composition described above. Therefore, the glass is suitable as an optical glass that gives a lighter optical element.

<Glass manufacturing method>
In order to obtain the desired glass composition, the glass is weighed and prepared as raw materials such as oxides, carbonates, sulfates, nitrates and hydroxides, and mixed well to form a mixed batch. It can be obtained by heating, melting, defoaming and stirring to make a molten glass free of bubbles and molding it. Specifically, it can be made using a known melting method. Although the above glass is a high refractive index low dispersion glass having the above-mentioned optical properties, it is excellent in thermal stability, and therefore can be stably produced using a known melting method and molding method.

[Press-molding glass material, optical element blank, and manufacturing method thereof]
Another aspect of the present invention is:
A glass material for press molding made of the glass described above;
Optical element blank made of the glass described above,
About.

According to another aspect of the invention,
A method for producing a glass material for press molding comprising a step of forming the glass described above into a glass material for press molding;
A method for producing an optical element blank comprising a step of producing an optical element blank by press-molding the above-described press-molding glass material using a press mold;
A method for producing an optical element blank, comprising a step of forming the glass described above into an optical element blank;
Is also provided.

  The optical element blank approximates the shape of the target optical element, and is polished to the shape of the optical element (surface layer to be removed by polishing) or ground as necessary (to be removed by grinding). An optical element base material to which a surface layer is added. The optical element is finished by grinding and polishing the surface of the optical element blank. In one embodiment, an optical element blank can be produced by a method of pressing a molten glass obtained by melting an appropriate amount of the glass (referred to as a direct press method). In another aspect, an optical element blank can be produced by solidifying a molten glass obtained by melting an appropriate amount of the glass.

  Moreover, in another one aspect | mode, an optical element blank can be produced by producing the glass material for press molding, and press-molding the produced glass material for press molding.

  Press molding of the glass material for press molding can be performed by a known method of pressing the glass material for press molding in a softened state by heating with a press mold. Both heating and press molding can be performed in the atmosphere. A uniform optical element blank can be obtained by annealing after press molding to reduce strain inside the glass.

  The glass material for press molding is subjected to mechanical processing such as cutting, grinding, polishing, etc. in addition to what is called glass gob for press molding used for press molding for optical element blank production as it is. It includes those that are subjected to press molding via As a cutting method, a groove is formed in a portion of the surface of the glass plate to be cut by a method called scribing, and a local pressure is applied to the groove portion from the back surface of the surface on which the groove is formed. There are a method of breaking a plate and a method of cutting a glass plate with a cutting blade. Moreover, barrel polishing etc. are mentioned as a grinding | polishing and a grinding | polishing method.

  The glass material for press molding can be produced, for example, by casting molten glass into a mold, forming a glass plate, and cutting the glass plate into a plurality of glass pieces. Alternatively, a glass gob for press molding can be produced by molding an appropriate amount of molten glass. An optical element blank can also be produced by repressing and softening a glass gob for press molding and press forming it. A method of producing an optical element blank by press-molding glass by reheating and softening is called a reheat press method as opposed to a direct press method.

[Optical element and manufacturing method thereof]
Another aspect of the present invention is:
The present invention relates to an optical element made of the glass.
The optical element is manufactured using the glass described above. In the optical element, one or more coatings such as a multilayer film such as an antireflection film may be formed on the glass surface.

According to one embodiment of the present invention,
A method for producing an optical element comprising a step of producing an optical element by grinding and / or polishing the optical element blank described above,
Is also provided.

  In the manufacturing method of the optical element, a known method may be applied for grinding and polishing, and an optical element having high internal quality and surface quality can be obtained by sufficiently washing and drying the surface of the optical element after processing. it can. In this way, an optical element made of the glass can be obtained. Examples of the optical element include various lenses such as a spherical lens, an aspheric lens, and a micro lens, a prism, and the like.

  The optical element made of glass is also suitable as a lens constituting the cemented optical element. Examples of the cemented optical element include those in which lenses are cemented (a cemented lens), and in which lenses and a prism are cemented. For example, the bonded optical element is an ultraviolet curable adhesive that is used for bonding a bonded lens by precisely processing (for example, spherical polishing) the bonded surface of two optical elements to be bonded so as to have an inverted shape. Can be produced by applying UV light through the lens and curing the adhesive. In order to produce a bonded optical element in this way, the glass is preferable. A plurality of optical elements to be bonded are manufactured using a plurality of types of glasses having different Abbe numbers νd, and bonded to each other, whereby an element suitable for correcting chromatic aberration can be obtained.

As a result of the quantitative analysis of the glass composition, the glass component may be expressed on an oxide basis, and the content of the glass component may be displayed in mass%. Thus, the composition represented by mass% on the basis of oxide can be converted into the composition represented by cation% and anion%, for example, by the following method.
If it contains N species of the glass component in the glass, a k-th of the glass component is denoted as A (k) _m O _n. However, k is an arbitrary integer of 1 or more and N or less.
A (k) is a cation, O is oxygen, and m and n are integers determined stoichiometrically. For example, when the notation based on the oxide is B ₂ O ₃ , m = 2 and n = 3, and in the case of SiO ₂ , m = 1 and n = 2.
Next, the content of A _(k) m _{O n,} and X (k) [wt%]. Here, A the atomic weight of (k) P (k), when the atomic number of oxygen O and Q, A _(k) m _{O n} formal molecular weight R of (k) is
R (k) = P (k) × m + Q × n
It becomes.
Furthermore,
B = 100 / {Σ [m × X (k) / R (k)]}
Then, the content (cation%) of the cation component A (k) ^{s +} is [X (k) / R (k)] × m × B (cation%). Here, Σ means the sum of m × X (k) / R (K) from k = 1 to N. m varies with k. s is 2 n / m.
Further, the molecular weight R (k) may be calculated using a value obtained by rounding off the fourth digit after the decimal point and displaying up to the third digit after the decimal point. Table 64 below shows the molecular weights of some glass components and additives in terms of oxide standards.

  Hereinafter, the present invention will be further described based on examples. However, the present invention is not limited to the embodiment shown in the examples.

Example 1
In order to obtain a glass having the composition shown in the table below, compounds such as oxide and boric acid were weighed as raw materials and mixed sufficiently to prepare batch raw materials.
This batch raw material was put into a platinum crucible, and the whole crucible was heated to a temperature of 1350 to 1450 ° C., and the glass was melted and clarified over 2 to 3 hours. After the molten glass was agitated and homogenized, the molten glass was cast into a preheated mold and allowed to cool to near the glass transition temperature, and then the glass together with the mold was placed in an annealing furnace. Then, annealing was performed for about 1 hour near the glass transition temperature. After annealing, it was allowed to cool to room temperature in an annealing furnace.
Observation of the glass thus prepared revealed no crystal precipitation, bubbles, striae, or unmelted raw material. In this way, highly homogenous glass could be made.

(Comparative Examples 1-4)
Implementation was conducted except that a batch raw material was prepared by weighing and thoroughly mixing compounds such as oxide and boric acid as raw materials so as to obtain glasses having the compositions of Comparative Examples 1 to 4 shown in the following table. Glass was obtained in the same manner as in Example 1.
The composition of Comparative Example 1 is the glass No. A composition in which the composition of 11 is converted to a glass composition represented by cation%,
Comparative Example 2 is glass No. 1 of Patent Document 20. A composition in which the composition of 25 is converted into a glass composition in terms of cation%,
Comparative Example 3 is glass No. 1 of Patent Document 20. A composition in which the composition of 45 is converted into a glass composition represented by cation%,
Comparative Example 4 is glass No. 5 of Patent Document 20. 49 composition converted to a glass composition of cation% display,
It is.

The glass characteristic of the obtained glass was measured by the method shown below. The measurement results are shown in the following table.
(1) Refractive index nd, nF, nc, ng, Abbe number νd
Refractive indexes nd, nF, nc, and ng were measured for the glass obtained by lowering the temperature at a temperature decrease rate of −30 ° C./hour by the refractive index measurement method of the Japan Optical Glass Industry Association standard. The Abbe number νd was calculated using the measured values of the refractive indexes nd, nF, and nc.
(2) Glass transition temperature Tg
Using a differential scanning calorimeter (DSC), the heating rate was 10 ° C./min.
(3) Specific gravity Measured by Archimedes method.
(4) Partial dispersion ratio Pg, F
It calculated from the value of nF, nc, ng measured by said (1).
(5) Liquidus temperature The glass was placed in a furnace heated to a predetermined temperature and held for 2 hours. After cooling, the inside of the glass was observed with a 100-fold optical microscope, and the liquidus temperature was determined from the presence or absence of crystals.

FIG. 1 shows the specific gravity of each glass of Example 1 and each glass of Comparative Examples 1 to 4 on the horizontal axis, and the vertical axis represents the sum D of values obtained by multiplying the content of each cationic component by the coefficient shown in Table 1. It is a graph taken in
As shown in FIG. 1, the total D obtained by multiplying the content of each cation component by the coefficient shown in Table 1 showed a good correlation with the specific gravity. From this result, it can be confirmed that low specific gravity glass can be obtained by adjusting the composition so as to satisfy the formula (B) based on the total D.

FIG. 2 is a graph in which the Abbe number νd of each glass of Example 1 and each glass of Comparative Examples 1 to 4 is taken on the horizontal axis, and the value A calculated by the above formula (A) is taken on the vertical axis.
As shown in FIG. 2, the value A calculated by the above equation (A) showed a good correlation with the Abbe number. From this result, it can be confirmed that the composition adjustment based on the value A is preferable in adjusting the Abbe number.

(Example 2)
Various glasses obtained in Example 1 were used to produce a press-molding glass lump (glass gob). This glass lump was heated and softened in the atmosphere, and press-molded with a press mold to produce a lens blank (optical element blank). The produced lens blank was taken out from the press mold, annealed, and machined including polishing, and spherical lenses made of various glasses produced in Example 1 were produced.

(Example 3)
A desired amount of the molten glass produced in Example 1 was press-molded with a press mold to produce a lens blank (optical element blank). The produced lens blank was taken out from the press mold, annealed, and machined including polishing, and spherical lenses made of various glasses produced in Example 1 were produced.

Example 4
A glass lump (optical element blank) produced by solidifying the molten glass produced in Example 1 was annealed and subjected to mechanical processing including polishing to produce spherical lenses made of various glasses produced in Example 1.

(Example 5)
The spherical lens produced in Examples 2-4 was bonded with the spherical lens which consists of another kind of glass, and the junction lens was produced. The cemented surfaces of the spherical lenses produced in Examples 2 to 4 were convex surfaces, and the cemented surfaces of spherical lenses made of other types of optical glass were concave surfaces. The two joint surfaces were produced so that the absolute values of the curvature radii were equal to each other. An ultraviolet curable adhesive for optical element bonding was applied to the bonding surface, and the two lenses were bonded to each other at the bonding surfaces. Thereafter, the adhesive applied to the joint surface was irradiated with ultraviolet rays through the spherical lenses prepared in Examples 2 to 4, and the adhesive was solidified.
A cemented lens was produced as described above. The cemented lens had a sufficiently high bonding strength and a sufficient level of optical performance.

  Finally, the above-described aspects are summarized.

According to one aspect, in terms of cation%, B ³⁺ , Si ⁴⁺ , La ³⁺ , Y ³⁺ , Gd ³⁺ , Yb ³⁺ , Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ , W ⁶⁺ , Zr ⁴⁺ , Zn ²⁺ , Mg ²⁺ , Ca ²⁺ , Sr ²⁺ , Ba ²⁺ , Li ⁺ , Na ⁺ , K ⁺ , Al ³⁺ , and Bi ³⁺ are 90% or more, and the Abbe number νd is in the range of 39.5 to 41.5. Yes, the refractive index nd satisfies the above formula (1) with respect to the Abbe number νd, and for the cation component described in Table 1, the total of the values of the content of each cation component multiplied by the coefficient described in Table 1 A glass in which D is an oxide glass that satisfies the above formula (B) with respect to the refractive index nd can be provided.

  The glass has a Abbe number νd in the range of 39.5 to 41.5 and satisfies the formula (1), and is a high refractive index and low dispersion glass useful in an optical system. Furthermore, the glass can contribute to weight reduction of the optical element.

In one aspect, the glass preferably has a total content of B ³⁺ and Si ^{4+ in} the range of 43 to 65 cation%.

In one embodiment, the glass preferably has a total content of La ³⁺ , Y ³⁺ , Gd ³⁺ and Yb ³⁺ in the range of 25 to 45%.

In one aspect, the glass preferably has a total content of Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ and W ⁶⁺ in the range of 3 to 12%.

  In one aspect, the glass preferably has a value C calculated from the above formula (C) in the range of −1.000 to 6.720 in the glass composition expressed in terms of cation%.

  From the glass described above, a glass material for press molding, an optical element blank, and an optical element can be produced. That is, according to another aspect, a glass material for press molding made of the above glass, an optical element blank, and an optical element are provided.

  Moreover, according to the other aspect, the manufacturing method of the glass material for press molding provided with the process of shape | molding the said glass to the glass material for press molding is also provided.

  According to still another aspect, there is also provided an optical element blank manufacturing method including a step of manufacturing an optical element blank by press-molding the press-molding glass material using a press mold.

  According to still another aspect, a method for producing an optical element blank including a step of forming the glass into an optical element blank is also provided.

  According to still another aspect, there is also provided an optical element manufacturing method including a step of manufacturing an optical element by grinding and / or polishing the optical element blank.

The embodiment disclosed this time should be considered as illustrative in all points and not restrictive. The scope of the present invention is defined by the terms of the claims, rather than the description above, and is intended to include any modifications within the scope and meaning equivalent to the terms of the claims.
For example, the glass concerning 1 aspect of this invention can be obtained by performing the composition adjustment as described in the specification with respect to the glass composition illustrated above.
Of course, it is possible to arbitrarily combine two or more of the matters described as examples or preferred ranges in the specification.

  The present invention is useful in the field of manufacturing various optical elements.

Claims (7)

In terms of cation%, B ³⁺ , Si ⁴⁺ , La ³⁺ , Y ³⁺ , Gd ³⁺ , Yb ³⁺ , Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ , W ⁶⁺ , Zr ⁴⁺ , Zn ²⁺ , Mg ²⁺ , Ca ²⁺ , Sr ²⁺ , Ba ²⁺ , Li ⁺ , Na ⁺ , K ⁺ , Al ³⁺ , and Bi ³⁺ are 90% or more,
The total content of La ³⁺ , Y ³⁺ , Gd ³⁺ and Yb ³⁺ is in the range of 28-45%,
Y ³⁺ content is in the range of 1-20%,
Abbe number νd is in the range of 39.5-41.5,
Refractive index nd is expressed by the following formula (1) with respect to Abbe number νd:
nd ≧ 2.0927−0.0058 × νd (1)
And the total D of the values obtained by multiplying the content of each cation component by the coefficient described in Table 1 with respect to the refractive index nd is the following formula (B):
D ≦ 6.224 × nd−6.8042 (B)
Glass which is oxide glass satisfying
In terms of cation%, B ³⁺ , Si ⁴⁺ , La ³⁺ , Y ³⁺ , Gd ³⁺ , Yb ³⁺ , Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ , W ⁶⁺ , Zr ⁴⁺ , Zn ²⁺ , Mg ²⁺ , Ca ²⁺ , Sr ²⁺ , Ba ²⁺ , Li ⁺ , Na ⁺ , K ⁺ , Al ³⁺ , and Bi ³⁺ are 90% or more,
The total content of La ³⁺ , Y ³⁺ , Gd ³⁺ and Yb ³⁺ is in the range of 28-45%,
The cation ratio of La ³⁺ content to the total content of La ³⁺ , Y ³⁺ , Gd ³⁺ and Yb ³⁺ {La ³⁺ / (La ³⁺ + Y ³⁺ + Gd ³⁺ + Yb ³⁺ ) is in the range of 0.50 to 0.95,
Abbe number νd is in the range of 39.5-41.5,
Refractive index nd is expressed by the following formula (1) with respect to Abbe number νd:
nd ≧ 2.0927−0.0058 × νd (1)
And the total D of the values obtained by multiplying the content of each cation component by the coefficient described in Table 1 with respect to the refractive index nd is the following formula (B):
D ≦ 6.224 × nd−6.8042 (B)
Glass which is oxide glass satisfying
The glass according to claim 1 or 2, wherein the total content of B ³⁺ and Si ⁴⁺ is in the range of 43 to 65 cation%. The glass according to claim 1, wherein the total content of Nb ⁵⁺ , Ti ⁴⁺ , Ta ⁵⁺ and W ⁶⁺ is in the range of 3 to 12%. The glass material for press molding which consists of the glass of any one of Claims 1-4. The optical element blank which consists of glass of any one of Claims 1-4. The optical element which consists of glass of any one of Claims 1-4.