TWI771744B - Optical glass and optical components - Google Patents

Optical glass and optical components Download PDF

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TWI771744B
TWI771744B TW109130194A TW109130194A TWI771744B TW I771744 B TWI771744 B TW I771744B TW 109130194 A TW109130194 A TW 109130194A TW 109130194 A TW109130194 A TW 109130194A TW I771744 B TWI771744 B TW I771744B
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glass
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TW202104113A (en
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武藤秀樹
藤原康裕
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日商Ｈｏｙａ股份有限公司
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    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/062—Glass compositions containing silica with less than 40% silica by weight
    • C03C3/064—Glass compositions containing silica with less than 40% silica by weight containing boron
    • C03C3/068—Glass compositions containing silica with less than 40% silica by weight containing boron containing rare earths
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/12—Silica-free oxide glass compositions
    • C03C3/14—Silica-free oxide glass compositions containing boron
    • C03C3/15—Silica-free oxide glass compositions containing boron containing rare earths
    • C03C3/155—Silica-free oxide glass compositions containing boron containing rare earths containing zirconium, titanium, tantalum or niobium
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C4/00—Compositions for glass with special properties
    • G—PHYSICS
    • G02—OPTICS
    • G02B—OPTICAL ELEMENTS, SYSTEMS OR APPARATUS
    • G02B1/00—Optical elements characterised by the material of which they are made; Optical coatings for optical elements

Abstract

本發明提供一種光學玻璃，該光學玻璃能夠降低原材料費等生產成本、熔融性和熱穩定性優秀，而且具有低溫軟化性的高折射率低色散。本發明還提供一種由該光學玻璃構成的光學元件和光學玻璃材料。在該光學玻璃中，RE1相對於NWF1的比[RE1/NWF1]為0.35以上；HR1相對於RE1的比[HR1/RE1]為0.33以下；Nb2 O5 的含量相對於Nb2 O5 和Ta2 O5 的合計含量的質量比[Nb2 O5 /(Nb2 O5 +Ta2 O5 )]為2/3以上；RE1相對於D1的比[RE1/D1]為0.90以上；L1相對於NWF1和RE1的合計值的比[L1/(NWF1+RE1)]為0.78以上；阿貝數(νd)為39.0以上、45.0以下，該阿貝數(νd)與折射率(nd)滿足下述式(1)：nd≥2.235-0.01×νd。The present invention provides an optical glass capable of reducing production costs such as raw material costs, excellent in meltability and thermal stability, and high refractive index and low dispersion with low temperature softening properties. The present invention also provides an optical element and an optical glass material composed of the optical glass. In this optical glass, the ratio of RE1 to NWF1 [RE1/NWF1] is 0.35 or more; the ratio of HR1 to RE1 [HR1/RE1] is 0.33 or less; the content of Nb 2 O 5 relative to Nb 2 O 5 and Ta The mass ratio of the total content of 2 O 5 [Nb 2 O 5 /(Nb 2 O 5 +Ta 2 O 5 )] is 2/3 or more; the ratio of RE1 to D1 [RE1/D1] is 0.90 or more; L1 is relatively The ratio [L1/(NWF1+RE1)] to the total value of NWF1 and RE1 is 0.78 or more; the Abbe number (νd) is 39.0 or more and 45.0 or less, and the Abbe number (νd) and the refractive index (nd) satisfy the following Formula (1): nd≥2.235-0.01×νd.

Description

光學玻璃及光學元件Optical glass and optical components

本發明關於一種光學玻璃，可降低製造成本、熔融性和熱穩定性優秀的高折射率低色散。本發明還關於一種由該光學玻璃構成的光學元件。The present invention relates to an optical glass, which can reduce the manufacturing cost, and has high refractive index and low dispersion excellent in meltability and thermal stability. The present invention also relates to an optical element composed of the optical glass.

通常，高折射率低色散的光學玻璃含有氧化硼和氧化鑭等稀土類氧化物。在這樣的光學玻璃中，為了在不減少阿貝數(Abbe number，νd)的情況下提高折射率，需要提高稀土類氧化物的含量。但是，當在這樣的光學玻璃中提高稀土類氧化物的含量時，玻璃的熱穩定性會下降，在製造玻璃的過程中玻璃會晶化，難以得到透明的玻璃(玻璃會失透(Devitrification))。因此，當在不減小阿貝數的情況下提高折射率時，製造光學玻璃將變得困難。Generally, optical glasses with high refractive index and low dispersion contain rare earth oxides such as boron oxide and lanthanum oxide. In such an optical glass, in order to increase the refractive index without decreasing the Abbe number (νd), it is necessary to increase the content of the rare earth oxide. However, when the content of rare earth oxides in such optical glass is increased, the thermal stability of the glass is lowered, the glass is crystallized during the production of the glass, and it is difficult to obtain a transparent glass (glass devitrification). ). Therefore, when the refractive index is increased without decreasing the Abbe number, it becomes difficult to manufacture optical glass.

另一方面，在光學系統的設計中，折射率高、阿貝數也大的光學玻璃在校正色像差、使光學系統高功能化、緊湊化方面的利用價值高。On the other hand, in the design of an optical system, an optical glass with a high refractive index and a large Abbe number has a high utility value in correcting chromatic aberration, and making the optical system highly functional and compact.

在具有高折射率低色散特性的玻璃中，適合於精密壓製成型的玻璃中大量地導入了具有使玻璃在低溫軟化的作用的鋅(Zn)或鋰(Li)。這樣的玻璃在專利文獻1～7中有所述。Among the glasses having high refractive index and low dispersion properties, zinc (Zn) or lithium (Li), which has the effect of softening the glass at low temperature, is introduced in a large amount into the glass suitable for precision press molding. Such glass is described in Patent Documents 1 to 7.

高折射率低色散玻璃，特別是具有在光學特性圖(也稱為阿貝圖表)中連接(阿貝數(νd)、折射率(nd))為A(45、1.785)和B(40、1.835)的2點的直線C上以及折射率(nd)比直線C高的範圍的光學特性的玻璃在光學設計上利用價值高。High-refractive-index, low-dispersion glasses, especially those with connections (Abbe number (νd), refractive index (nd)) in optical property diagrams (also known as Abbe diagrams) of A (45, 1.785) and B (40, 1.835) on the straight line C at 2 points and the glass with optical properties in the range where the refractive index (nd) is higher than the straight line C is highly useful in optical design.

另一方面，如專利文獻1、2、6所述的那樣，為了在維持熱穩定性的同時降低玻璃化轉變溫度(Tg)，這種玻璃需要導入大量的氧化鉭。但是，氧化鉭稀少且價值高，不容易作為玻璃原料而得到穩定的供給。此外，氧化鉭的價格極高，成為使玻璃的價格上升的原因。On the other hand, as described in Patent Documents 1, 2, and 6, in order to lower the glass transition temperature (Tg) while maintaining thermal stability, it is necessary to introduce a large amount of tantalum oxide into such a glass. However, tantalum oxide is rare and valuable, and it is not easy to obtain a stable supply as a glass raw material. In addition, the price of tantalum oxide is extremely high, which causes the price of glass to rise.

另一方面，在專利文獻3～5、7中公開了削減了鉭(Ta)的含量的玻璃，但是其折射率比上述直線C低，不滿足光學設計方面的要求。On the other hand, Patent Documents 3 to 5 and 7 disclose glasses in which the content of tantalum (Ta) is reduced, but the refractive index is lower than the above-mentioned straight line C, which does not satisfy the requirements of optical design.

此外，要求改善光學玻璃的熔融性。藉由改善玻璃的熔融性，從而對於透射率和澄清性能夠期待令人滿意的改善效果。具體如下。In addition, it is required to improve the meltability of optical glass. By improving the meltability of glass, a satisfactory improvement effect can be expected with respect to transmittance and clarity. details as follows.

首先，說明改善熔融性對透射率的影響。First, the effect of improving meltability on transmittance will be described.

通常，在熔融性差的玻璃的情況下，存在玻璃原料在玻璃中產生熔融殘留的問題。這樣的玻璃原料的熔融殘留會導致玻璃組成的改變、玻璃的均質性變差。因此，通常會提高熔融溫度、延長熔融時間來進行製造，使得不會產生玻璃原料的熔融殘留。In general, in the case of glass with poor melting properties, there is a problem that glass raw materials remain melted in the glass. Such molten residues of glass raw materials cause changes in glass composition and deterioration of glass homogeneity. Therefore, generally, the melting temperature is increased and the melting time is prolonged to manufacture so that the melting residue of the glass raw material does not occur.

但是，雖然提高熔融溫度、延長熔融時間可消除玻璃原料的熔融殘留的問題，但是會招致熔融容器劣化、生產成本增大這樣的新問題。特別是，熔融玻璃對熔融容器的侵蝕是個大問題。However, while increasing the melting temperature and prolonging the melting time can eliminate the problem of residual melting of the glass raw material, new problems such as deterioration of the melting vessel and increase in production cost are caused. In particular, the erosion of molten glass to the melting vessel is a big problem.

通常，在熔融像光學玻璃那樣要求高均質性的玻璃時，作為熔融容器而廣泛使用鉑製坩堝等貴金屬制坩堝。與由其它材料構成的坩堝相比，貴金屬製的坩堝不易受到熔融玻璃的侵蝕。但是，如上所述，在將熔融性差的玻璃進行熔融的情況下，高溫的熔融玻璃與坩堝長時間接觸，因此即使是貴金屬製的坩堝也會受到熔融玻璃的侵蝕。Generally, when melting glass requiring high homogeneity like optical glass, a crucible made of precious metal such as a platinum crucible is widely used as a melting vessel. Crucibles made of precious metals are less susceptible to corrosion by molten glass than crucibles made of other materials. However, as described above, when melting glass with poor melting properties, the high-temperature molten glass is in contact with the crucible for a long period of time, so even a crucible made of a precious metal is corroded by the molten glass.

例如，在鉑製坩堝的情況下，有時會由於熔融玻璃的侵蝕而使構成坩堝的鉑作為固體而混入到熔融玻璃中。這樣的固體在玻璃中會成為雜質而成為光的散射源。此外，當坩堝被輕微地侵蝕而使鉑作為離子溶入到熔融玻璃時，由於溶入到玻璃中的鉑離子的光吸收，作為產品的光學玻璃的著色會增強、可見光區域的透射率會降低。For example, in the case of a platinum crucible, platinum constituting the crucible may be mixed into the molten glass as a solid due to erosion of the molten glass. Such a solid becomes an impurity in glass and becomes a scattering source of light. In addition, when the crucible is slightly eroded to dissolve platinum as ions into the molten glass, the coloring of the optical glass as a product increases due to light absorption by the platinum ions dissolved in the glass, and the transmittance in the visible light region decreases. .

另一方面，如果是熔融性優秀的玻璃，則不易產生玻璃原料的熔融殘留的問題。因此，不需要提高熔融溫度、延長熔融時間，能夠抑制熔融玻璃對熔融容器的侵蝕。進而，還能抑制熔融溫度的高溫化、熔融時間的延長導致的玻璃的透射率的降低。On the other hand, in the case of glass having excellent meltability, the problem of melting residues of glass raw materials is less likely to occur. Therefore, it is not necessary to increase the melting temperature and prolong the melting time, and it is possible to suppress the erosion of the melting vessel by the molten glass. Furthermore, it is possible to suppress the decrease in the transmittance of the glass due to an increase in the melting temperature and prolongation of the melting time.

即，藉由改善熔融性，從而能夠改善玻璃的均質性並且抑制可見光區域的透射率降低。That is, by improving the meltability, it is possible to improve the homogeneity of the glass and suppress the decrease in transmittance in the visible light region.

接著，說明改善熔融性對澄清性的影響。Next, the effect of improving the meltability on the clarity will be described.

通常，在將批料原料(調配了複數種化合物的原料)粗熔解(rough melt)而製作碎玻璃原料、將碎玻璃原料再熔融(remelt)而製造光學玻璃的方法(粗熔解-再熔融方式)中，在改善再熔融的熔融玻璃的消泡(即，改善澄清性(脫泡性))時，較佳碎玻璃中包含的氣體成分大量溶解在澄清前的熔融玻璃中，即，較佳提高澄清前的熔融玻璃中的氣體成分的溶解量。In general, a method (rough melting-remelting method) in which a batch raw material (raw material prepared with a plurality of compounds) is roughly melted to produce a cullet raw material, and a cullet raw material is remelted to produce an optical glass (rough melting-remelting method). ), when improving the defoaming of the remelted molten glass (that is, improving the clarification (defoaming property)), it is preferable that a large amount of gas components contained in the cullet dissolve in the molten glass before clarification, that is, it is preferable that The dissolved amount of the gas component in the molten glass before clarification is increased.

在此，氣體成分例如是批料原料所包含的硼酸、碳酸鹽、硝酸鹽、硫酸鹽、氫氧化物等被加熱、分解而產生的水蒸氣、COx 、NOx 及SOx 等氣體。Here, the gas component is, for example, gases such as water vapor, CO x , NO x and SO x generated by heating and decomposing boric acid, carbonate, nitrate, sulfate, hydroxide and the like contained in the batch raw material.

如上所述，在製造熔融性差的玻璃時，需要提高熔融溫度、延長熔融時間來進行製造，使得不會產生玻璃原料的熔融殘留。特別是，在高溫下容易從批料原料的熔融物釋放出來自原料的氣體，如果粗熔解的時間再變長，碎玻璃中就不會留下足夠的氣體成分。As described above, when producing glass with poor melting properties, it is necessary to increase the melting temperature and prolong the melting time so that the melting residue of the glass raw material does not occur. In particular, the gas from the raw material is easily released from the melt of the batch raw material at high temperature, and if the time for rough melting is longer, sufficient gas components will not remain in the cullet.

通常，藉由將碎玻璃再熔融，從而殘存在碎玻璃中的氣體成分會在熔融玻璃中成為氣泡，與微小的氣泡一起形成大的氣泡。關於熔融玻璃中的氣泡，相比微小的氣泡，大的氣泡在熔融玻璃中上浮的速度更快，可迅速到達熔融玻璃的液面，排出到熔融玻璃外。因此，能夠在短時間內進行熔融玻璃的澄清。但是，在像上述那樣熔融性差的玻璃的情況下，碎玻璃中沒有殘存足夠量的氣體成分，因此難以使微小的氣泡生長為大的氣泡，微小的氣泡難以排出到熔融玻璃外。因此，不能進行充分的澄清，導致在作為產品的光學玻璃中殘留有微小的氣泡的問題。Usually, by remelting the cullet, the gas component remaining in the cullet becomes bubbles in the molten glass, and together with the fine bubbles, large bubbles are formed. Regarding the air bubbles in the molten glass, the large air bubbles float faster in the molten glass than the minute air bubbles, and can quickly reach the liquid level of the molten glass and be discharged to the outside of the molten glass. Therefore, the clarification of molten glass can be performed in a short time. However, in the case of glass with poor melting properties as described above, since a sufficient amount of gas components does not remain in the cullet, it is difficult to grow microscopic bubbles into large ones, and it is difficult for microscopic bubbles to be discharged out of the molten glass. Therefore, sufficient clarification cannot be performed, and there is a problem that minute air bubbles remain in the optical glass as a product.

另一方面，在熔融性優秀的玻璃的粗熔解中，能夠以較低溫度熔融批料原料。因此，能夠以熔融物中溶入了大量氣體成分的狀態製作碎玻璃。其結果是，只要使用這樣的碎玻璃，就能夠在較短時間內澄清熔融玻璃。On the other hand, in the rough melting of glass having excellent meltability, the batch raw material can be melted at a relatively low temperature. Therefore, a cullet can be produced in the state which melt|dissolved a large amount of gas components in a melt. As a result, if such a cullet is used, a molten glass can be clarified in a relatively short time.

即，藉由改善熔融性，從而能夠改善玻璃的澄清性，能夠增加每單位時間的玻璃的生產量。That is, by improving the meltability, the clarity of the glass can be improved, and the throughput of the glass per unit time can be increased.

如上所述，藉由改善熔融性，從而不僅能夠改善玻璃的透射率，還能夠改善澄清性。此外，藉由改善熔融性，從而能夠降低玻璃的熔融所消耗的能量，還能夠縮短熔融時間，因此還能夠期待生產成本降低、生產率提高。像這樣，可以說改善熔融性是非常有益的。 [先前技術文獻] [專利文獻]As described above, by improving the meltability, not only the transmittance of the glass but also the clarity can be improved. Further, by improving the meltability, the energy consumed for melting the glass can be reduced, and the melting time can be shortened, so that production cost reduction and productivity improvement can also be expected. In this way, it can be said that improving the meltability is very beneficial. [Prior Art Literature] [Patent Literature]

專利文獻1：美國專利第7897533號。 專利文獻2：日本特開2003-201142。 專利文獻3：日本特開2002-012443。 專利文獻4：日本特表2009-537427。 專利文獻5：日本特開2003-201142。 專利文獻6：日本特開2009-203083。 專利文獻7：日本特表2009-537427。Patent Document 1: US Pat. No. 7,897,533. Patent Document 2: Japanese Patent Laid-Open No. 2003-201142. Patent Document 3: Japanese Patent Laid-Open No. 2002-012443. Patent Document 4: Japanese Patent Application Laid-Open No. 2009-537427. Patent Document 5: Japanese Patent Laid-Open No. 2003-201142. Patent Document 6: Japanese Patent Laid-Open No. 2009-203083. Patent Document 7: Japanese Patent Application Laid-Open No. 2009-537427.

(發明所欲解決的課題)(The problem to be solved by the invention)

本發明是鑒於這樣的實際情況而完成的，其一目的在於提供一種光學玻璃，該光學玻璃能夠降低原材料費等生產成本、熔融性和熱穩定性優秀，並且具有低溫軟化性的高折射率低色散。本發明的目的還在於提供一種由該光學玻璃構成的光學元件及光學玻璃材料。 (用以解決課題之手段)The present invention has been made in view of such a situation, and an object of the present invention is to provide an optical glass which can reduce production costs such as raw material costs, is excellent in meltability and thermal stability, and has low temperature softening properties, a high refractive index and a low refractive index. dispersion. Another object of the present invention is to provide an optical element and an optical glass material composed of the optical glass. (means to solve the problem)

本發明人為了達到上述目的而進行了反復深入研究，結果發現，藉由降低作為比較昂貴的材料的氧化鉭的使用量並且調整構成玻璃的各種玻璃構成成分(以下，稱為玻璃成分)的含有比例的平衡可達到該目的，並基於該認識完成了本發明。The inventors of the present invention have conducted intensive studies in order to achieve the above-mentioned object, and as a result, have found that by reducing the amount of tantalum oxide used as a relatively expensive material and adjusting the content of various glass constituent components (hereinafter, referred to as glass components) constituting glass The balance of the ratios can achieve this object, and the present invention has been completed based on this knowledge.

即，本發明的要點如下。 (1)一種光學玻璃，在該光學玻璃中，RE1相對於NWF1的比[RE1/NWF1]為0.35以上；HR1相對於RE1的比[HR1/RE1]為0.33以下；Nb2 O5 的含量相對於Nb2 O5 和Ta2 O5 的合計含量的質量比[Nb2 O5 /(Nb2 O5 +Ta2 O5 )]為2/3以上；RE1相對於D1的比[RE1/D1]為0.90以上；L1相對於NWF1和RE1的合計值的比[L1/(NWF1+RE1)]為0.78以上；阿貝數(νd)為39.0以上、45.0以下，該阿貝數(νd)與折射率(nd)滿足下述式(1)：nd≥2.235-0.01×νdThat is, the gist of the present invention is as follows. (1) An optical glass in which the ratio of RE1 to NWF1 [RE1/NWF1] is 0.35 or more; the ratio of HR1 to RE1 [HR1/RE1] is 0.33 or less; the content of Nb 2 O 5 is relatively The mass ratio to the total content of Nb 2 O 5 and Ta 2 O 5 [Nb 2 O 5 /(Nb 2 O 5 +Ta 2 O 5 )] is 2/3 or more; the ratio of RE1 to D1 [RE1/D1 ] is 0.90 or more; the ratio of L1 to the total value of NWF1 and RE1 [L1/(NWF1+RE1)] is 0.78 or more; the Abbe number (νd) is 39.0 or more and 45.0 or less, the Abbe number (νd) and The refractive index (nd) satisfies the following formula (1): nd≥2.235-0.01×νd

式中：當將M(B2 O3 )、M(SiO2 )、M(Al2 O3 )、M(La2 O3 )、M(Gd2 O3 )、M(Y2 O3 )、M(Yb2 O3 )、M(LaF3 )、M(GdF3 )、M(YF3 )、M(YbF3 )、M(ZnO)、M(Li2 O)、M(Na2 O)、M(K2 O)、M(ZrO2 )、M(Nb2 O5 )、M(TiO2 )、M(WO3 )、M(Ta2 O5 )、M(Bi2 O3 )、M(MgO)、M(CaO)、M(SrO)、M(BaO)分別設為B2 O3 、SiO2 、Al2 O3 、La2 O3 、Gd2 O3 、Y2 O3 、Yb2 O3 、LaF3 、GdF3 、YF3 、YbF3 、ZnO、Li2 O、Na2 O、K2 O、ZrO2 、Nb2 O5 、TiO2 、WO3 、Ta2 O5 、Bi2 O3 、MgO、CaO、SrO、BaO的分子量時：NWF1=[2 ×B2 O3 /M(B2 O3 )]+[SiO2 /M(SiO2 )]+[2×Al2 O3 /M(Al2 O3 )]；RE1=[2 ×La2 O3 /M(La2 O3 )]+[2×Gd2 O3 /M(Gd2 O3 )]+[2×Y2 O3 /M(Y2 O3 )]+[2×Yb2 O3 /M(Yb2 O3 )]+[LaF3 /M(LaF3 )]+[GdF3 /M(GdF3 )]+[YF3 /M(YF3 )]+[YbF3 /M(YbF3 )]；HR1=[2×Nb2 O5 /M(Nb2 O5 )]+[TiO2 /M (TiO2 )]+[WO3 /M(WO3 )]+[2×Bi2 O3 /M(Bi2 O3 )]；D1={[2×Li2 O/M (Li2 O)]+[2×Na2 O/M(Na2 O)]+[2×K2 O/M(K2 O)]}×3+[ZnO/M(ZnO)]；L1=[20×Li2 O/M(Li2 O)]+[16×Na2 O/M(Na2 O)]+[8×K2 O/M (K2 O)]+[4×ZnO/M(ZnO)]+[MgO/M(MgO)]+[2×CaO/M(CaO)]+[2×SrO/M(SrO)]+[2×BaO/M(BaO)]+[2×B2 O3 /M(B2 O3 )]+[2×Nb2 O5 /M(Nb2 O5 )]+[TiO2 /M(TiO2 )]+[4×WO3 /M(WO3 )]+[8×Bi2 O3 /M(Bi2 O3 )]+[2×Ta2 O5 /M(Ta2 O5 )]-[2×SiO2 /M(SiO2 )]-[2×Al2 O3 /M(Al2 O3 )]-[2×ZrO2 /M(ZrO2 )]-[2×La2 O3 /M(La2 O3 )]-[2×Gd2 O3 /M(Gd2 O3 )]-[2×Y2 O3 /M(Y2 O3 )]-[2×Yb2 O3 /M(Yb2 O3 )]-[LaF3 /M(LaF3 )]-[GdF3 /M(GdF3 )]-[YF3 /M(YF3 )]-[YbF3 /M(YbF3 )]；上述各玻璃成分的含量為以質量%表示的值。In the formula: when M(B 2 O 3 ), M(SiO 2 ), M(Al 2 O 3 ), M(La 2 O 3 ), M(Gd 2 O 3 ), M(Y 2 O 3 ) , M(Yb 2 O 3 ), M(LaF 3 ), M(GdF 3 ), M(YF 3 ), M(YbF 3 ), M(ZnO), M(Li 2 O), M(Na 2 O ), M(K 2 O), M(ZrO 2 ), M(Nb 2 O 5 ), M(TiO 2 ), M(WO 3 ), M(Ta 2 O 5 ), M(Bi 2 O 3 ) , M(MgO), M(CaO), M(SrO), M(BaO) are B 2 O 3 , SiO 2 , Al 2 O 3 , La 2 O 3 , Gd 2 O 3 , Y 2 O 3 , respectively , Yb 2 O 3 , LaF 3 , GdF 3 , YF 3 , YbF 3 , ZnO, Li 2 O, Na 2 O, K 2 O, ZrO 2 , Nb 2 O 5 , TiO 2 , WO 3 , Ta 2 O 5 , Bi 2 O 3 , MgO, CaO, SrO, BaO molecular weight: NWF1=[2×B 2 O 3 /M(B 2 O 3 )]+[SiO 2 /M(SiO 2 )]+[2× Al 2 O 3 /M(Al 2 O 3 )]; RE1=[2 ×La 2 O 3 /M(La 2 O 3 )]+[2×Gd 2 O 3 /M(Gd 2 O 3 )]+ [2×Y 2 O 3 /M(Y 2 O 3 )]+[2×Yb 2 O 3 /M(Yb 2 O 3 )]+[LaF 3 /M(LaF 3 )]+[GdF 3 /M (GdF 3 )]+[YF 3 /M(YF 3 )]+[YbF 3 /M(YbF 3 )]; HR1=[2×Nb 2 O 5 /M(Nb 2 O 5 )]+[TiO 2 /M (TiO 2 )]+[WO 3 /M(WO 3 )]+[2×Bi 2 O 3 /M(Bi 2 O 3 )]; D1={[2×Li 2 O/M (Li 2 O)]+[2×Na 2 O/M(Na 2 O)]+[2×K 2 O/M(K 2 O)]}×3+[ZnO/M(ZnO)]; L1=[20 ×Li 2 O/M(Li 2 O)]+[16×Na 2 O/M(Na 2 O)]+[8×K 2 O/M (K 2 O)]+[4×ZnO/M( ZnO)]+[MgO/M(MgO)]+[2×CaO/M(CaO)] +[2×SrO/M(SrO)]+[2×BaO/M(BaO)]+[2×B 2 O 3 /M(B 2 O 3 )]+[2×Nb 2 O 5 /M( Nb 2 O 5 )]+[TiO 2 /M(TiO 2 )]+[4×WO 3 /M(WO 3 )]+[8×Bi 2 O 3 /M(Bi 2 O 3 )]+[2 ×Ta 2 O 5 /M(Ta 2 O 5 )]-[2×SiO 2 /M(SiO 2 )]-[2×Al 2 O 3 /M(Al 2 O 3 )]-[2×ZrO 2 /M(ZrO 2 )]-[2×La 2 O 3 /M(La 2 O 3 )]-[2×Gd 2 O 3 /M(Gd 2 O 3 )]-[2×Y 2 O 3 / M(Y 2 O 3 )]-[2×Yb 2 O 3 /M(Yb 2 O 3 )]-[LaF 3 /M(LaF 3 )]-[GdF 3 /M(GdF 3 )]-[YF 3 /M(YF 3 )]-[YbF 3 /M(YbF 3 )]; the content of each of the above-mentioned glass components is a value represented by mass %.

(2)一種光學玻璃，該光學玻璃是氧化物玻璃，在該光學玻璃中，RE2相對於NWF2的比[RE2/NWF2]為0.35以上；HR2相對於RE2的比[HR2/RE2]為0.33以下；Nb5+ 的含量相對於Nb5+ 和Ta5+ 的合計含量的陽離子比[Nb5+ /(Nb5+ +Ta5+ )]為3/4以上；RE2相對於D2的比[RE2/D2]為0.90以上；L2相對於NWF2和RE2的合計值的比[L2/(NWF2+RE2)]為0.78以上；阿貝數(νd)為39.0以上、45.0以下，該阿貝數(νd)與折射率(nd)滿足下述式(1)：nd≥2.235-0.01×νd(2) An optical glass, which is an oxide glass, in which the ratio of RE2 to NWF2 [RE2/NWF2] is 0.35 or more, and the ratio of HR2 to RE2 [HR2/RE2] is 0.33 or less ; The cation ratio of the content of Nb 5+ to the total content of Nb 5+ and Ta 5+ [Nb 5+ /(Nb 5+ +Ta 5+ )] is 3/4 or more; the ratio of RE2 to D2 [RE2 /D2] is 0.90 or more; the ratio of L2 to the total value of NWF2 and RE2 [L2/(NWF2+RE2)] is 0.78 or more; the Abbe number (νd) is 39.0 or more and 45.0 or less, the Abbe number (νd ) and the refractive index (nd) satisfy the following formula (1): nd≥2.235-0.01×νd

式中：NWF2為B3+ 、Si4+ 及Al3+ 的合計含量；RE2為La3+ 、Gd3+ 、Y3+ 及Yb3+ 的合計含量；HR2為Nb5+ 、Ti4+ 、W6+ 及Bi3+ 的合計含量；D2=(Li+ +Na+ +K+ )×6+Zn2+ ；L2= (10×Li+ )+(8×Na+ )+(4×K+ )+(4×Zn+ )+Mg2+ +(2×Ca2+ )+(2×Sr2+ )+(2×Ba2+ )+B3+ +Nb5+ +Ti4+ +(4×W6+ )+(4×Bi3+ )+Ta5+ -(2×Si4+ )-Al3+ -(2×Zr4+ )-La3+ -Gd3+ -Y3+ -Yb3+ ；上述各玻璃成分的含量為以陽離子%表示的值。In the formula: NWF2 is the total content of B 3+ , Si 4+ and Al 3+ ; RE2 is the total content of La 3+ , Gd 3+ , Y 3+ and Yb 3+ ; HR2 is Nb 5+ , Ti 4+ , W 6+ and Bi 3+ total content; D2=(Li + +Na + +K + )×6+Zn 2+ ; L2=(10×Li + )+(8×Na + )+(4× K + )+(4×Zn + )+Mg 2+ +(2×Ca 2+ )+(2×Sr 2+ )+(2×Ba 2+ )+B 3+ +Nb 5+ +Ti 4+ +(4×W 6+ )+(4×Bi 3+ )+Ta 5+ -(2×Si 4+ )-Al 3+ -(2×Zr 4+ )-La 3+ -Gd 3+ -Y 3+ -Yb 3+ ; the content of each of the above-mentioned glass components is a value represented by cation %.

(3)一種精密壓製成型用預製件，由上述(1)或(2)所述的光學玻璃構成。(3) A preform for precision press molding, comprising the optical glass according to (1) or (2) above.

(4)一種光學元件，由上述(1)或(2)所述的光學玻璃構成。 (發明功效)(4) An optical element comprising the optical glass described in (1) or (2) above. (Inventive effect)

根據本發明，能夠提供可降低生產成本、熔融性和熱穩定性優秀，並且具有低溫軟化性的高折射率低色散的光學玻璃及使用該光學玻璃的光學元件。According to the present invention, it is possible to provide a high-refractive-index, low-dispersion optical glass that can reduce production costs, is excellent in meltability and thermal stability, and has low-temperature softening properties, and an optical element using the optical glass.

以下，對用於實施本發明的形態(以下簡稱為“實施形態”)進行詳細說明。以下的本實施形態是用於說明本發明的例示，其宗旨不是將本發明限定為以下的內容。本發明能夠在其要點的範圍內適當地變形而實施。進而，對於說明重複的部分有時會適當地省略說明，但其並不限定發明的宗旨。另外，在本說明書中，“光學玻璃”是包含複數種玻璃構成成分(玻璃成分)的玻璃組合物，用作與形狀(塊狀、板狀、球狀等)、用途(光學元件用材料、光學元件等)、大小無關的統稱。即，對光學玻璃的形狀、用途、大小沒有限制，任何形狀的光學玻璃、任何用途的光學玻璃、以及任何大小的光學玻璃均屬於本發明的光學玻璃。此外，在本說明書中，有時將光學玻璃簡稱為“玻璃”。Hereinafter, an embodiment for implementing the present invention (hereinafter simply referred to as an "embodiment") will be described in detail. The following present embodiments are examples for explaining the present invention, and are not intended to limit the present invention to the following contents. The present invention can be appropriately modified and implemented within the scope of its gist. Furthermore, the description may be appropriately omitted for portions where the description overlaps, but this does not limit the gist of the invention. In addition, in this specification, "optical glass" is a glass composition containing a plurality of glass constituent components (glass components), and is used for shapes (block, plate, spherical, etc.), applications (materials for optical elements, Optical components, etc.), size-independent general term. That is, the shape, use, and size of the optical glass are not limited, and optical glass of any shape, optical glass of any purpose, and optical glass of any size belong to the optical glass of the present invention. In addition, in this specification, optical glass may be abbreviated as "glass" in some cases.

此外，在本說明書中，有時使用(數值1)以“(數值1)以下”的方式來表示數值範圍。這樣表示的範圍是小於(數值1)的數值範圍加上(數值1)的數值範圍。以“不足(數值1)”表示的數值範圍是小於(數值1)的數值範圍，不包含(數值1)。有時使用(數值2)以“(數值2)以上”的方式來表示數值範圍。這樣表示的範圍是大於(數值2)的數值範圍加上(數值2)的數值範圍。有時以“超過(數值2)”的方式來表示數值範圍。這樣表示的範圍是大於(數值2)大的數值範圍，不包含(數值2)。In addition, in this specification, (numerical value 1) may be used to express a numerical range in the form of "(numerical value 1) or less". The range thus expressed is the range of values less than (numerical 1) plus the range of numerical values of (numerical 1). The numerical range represented by "less than (numerical value 1)" is a numerical value range less than (numerical value 1) and does not include (numerical value 1). (Numerical 2) is sometimes used to express a numerical range in the form of "(Numerical 2) or more". The range thus expressed is the numerical range greater than (numerical 2) plus the numerical range of (numerical 2). Numerical ranges are sometimes expressed as "exceeds (numerical 2)". The range indicated in this way is a numerical range larger than (numerical value 2) and does not include (numerical value 2).

首先，作為第1實施形態對以質量%表示的玻璃組成進行說明，接著作為第2實施形態對以陽離子%表示的玻璃組成進行說明。First, the glass composition represented by mass % will be described as the first embodiment, and then the glass composition represented by cation % will be described as the second embodiment.

第1實施形態 (以質量%表示的組成) 以下，以氧化物為基準的形式來表示玻璃組成。first embodiment (composition in mass %) Hereinafter, the glass composition will be represented on the basis of oxides.

本發明的第1實施形態的光學玻璃為如下的光學玻璃，在該光學玻璃中，RE1相對於NWF1的比[RE1/NWF1]為0.35以上；HR1相對於RE1的比[HR1/RE1]為0.33以下；Nb2 O5 的含量相對於Nb2 O5 和Ta2 O5 的合計含量的質量比[Nb2 O5 /(Nb2 O5 +Ta2 O5 )]為2/3以上；RE1相對於D1的比[RE1/D1]為0.90以上；L1相對於NWF1和RE1的合計值的比[L1/(NWF1+RE1)]為0.78以上；阿貝數(νd)為39.0以上、45.0以下，該阿貝數(νd)與折射率(nd)滿足下述式(1)：nd≥2.235-0.01×νdThe optical glass according to the first embodiment of the present invention is an optical glass in which the ratio of RE1 to NWF1 [RE1/NWF1] is 0.35 or more, and the ratio of HR1 to RE1 [HR1/RE1] is 0.33 or less; the mass ratio of the content of Nb 2 O 5 to the total content of Nb 2 O 5 and Ta 2 O 5 [Nb 2 O 5 /(Nb 2 O 5 +Ta 2 O 5 )] is 2/3 or more; RE1 The ratio [RE1/D1] to D1 is 0.90 or more; the ratio of L1 to the total value of NWF1 and RE1 [L1/(NWF1+RE1)] is 0.78 or more; the Abbe number (νd) is 39.0 or more and 45.0 or less , the Abbe number (νd) and the refractive index (nd) satisfy the following formula (1): nd≥2.235-0.01×νd

式中：當將M(B2 O3 )、M(SiO2 )、M(Al2 O3 )、M(La2 O3 )、M(Gd2 O3 )、M(Y2 O3 )、M(Yb2 O3 )、M(LaF3 )、M(GdF3 )、M(YF3 )、M(YbF3 )、M(ZnO)、M(Li2 O)、M(Na2 O)、M(K2 O)、M(ZrO2 )、M(Nb2 O5 )、M(TiO2 )、M(WO3 )、M(Ta2 O5 )、M(Bi2 O3 )、M(MgO)、M(CaO)、M(SrO)、M(BaO)分別設為B2 O3 、SiO2 、Al2 O3 、La2 O3 、Gd2 O3 、Y2 O3 、Yb2 O3 、LaF3 、GdF3 、YF3 、YbF3 、ZnO、Li2 O、Na2 O、K2 O、ZrO2 、Nb2 O5 、TiO2 、WO3 、Ta2 O5 、Bi2 O3 、MgO、CaO、SrO、BaO的分子量時：NWF1=[2 ×B2 O3 /M(B2 O3 )]+[SiO2 /M(SiO2 )]+[2×Al2 O3 /M(Al2 O3 )]；RE1=[2 ×La2 O3 /M(La2 O3 )]+[2×Gd2 O3 /M(Gd2 O3 )]+[2×Y2 O3 /M(Y2 O3 )]+[2×Yb2 O3 /M(Yb2 O3 )]+[LaF3 /M(LaF3 )]+[GdF3 /M(GdF3 )]+[YF3 /M(YF3 )]+[YbF3 /M(YbF3 )]；HR1=[2×Nb2 O5 /M(Nb2 O5 )]+[TiO2 /M (TiO2 )]+[WO3 /M(WO3 )]+[2×Bi2 O3 /M(Bi2 O3 )]；D1={[2×Li2 O/M (Li2 O)]+[2×Na2 O/M(Na2 O)]+[2×K2 O/M(K2 O)]}×3+[ZnO/M(ZnO)]；L1=[20×Li2 O/M(Li2 O)]+[16×Na2 O/M(Na2 O)]+[8×K2 O/M (K2 O)]+[4×ZnO/M(ZnO)]+[MgO/M(MgO)]+[2×CaO/M(CaO)]+[2×SrO/M(SrO)]+[2×BaO/M(BaO)]+[2×B2 O3 /M(B2 O3 )]+[2×Nb2 O5 /M(Nb2 O5 )]+[TiO2 /M(TiO2 )]+[4×WO3 /M(WO3 )]+[8×Bi2 O3 /M(Bi2 O3 )]+[2×Ta2 O5 /M(Ta2 O5 )]-[2×SiO2 /M(SiO2 )]-[2×Al2 O3 /M(Al2 O3 )]-[2×ZrO2 /M(ZrO2 )]-[2×La2 O3 /M(La2 O3 )]-[2×Gd2 O3 /M(Gd2 O3 )]-[2×Y2 O3 /M(Y2 O3 )]-[2×Yb2 O3 /M(Yb2 O3 )]-[LaF3 /M(LaF3 )]-[GdF3 /M(GdF3 )]-[YF3 /M(YF3 )]-[YbF3 /M(YbF3 )]；上述各玻璃成分的含量是以質量%表示的值。In the formula: when M(B 2 O 3 ), M(SiO 2 ), M(Al 2 O 3 ), M(La 2 O 3 ), M(Gd 2 O 3 ), M(Y 2 O 3 ) , M(Yb 2 O 3 ), M(LaF 3 ), M(GdF 3 ), M(YF 3 ), M(YbF 3 ), M(ZnO), M(Li 2 O), M(Na 2 O ), M(K 2 O), M(ZrO 2 ), M(Nb 2 O 5 ), M(TiO 2 ), M(WO 3 ), M(Ta 2 O 5 ), M(Bi 2 O 3 ) , M(MgO), M(CaO), M(SrO), M(BaO) are B 2 O 3 , SiO 2 , Al 2 O 3 , La 2 O 3 , Gd 2 O 3 , Y 2 O 3 , respectively , Yb 2 O 3 , LaF 3 , GdF 3 , YF 3 , YbF 3 , ZnO, Li 2 O, Na 2 O, K 2 O, ZrO 2 , Nb 2 O 5 , TiO 2 , WO 3 , Ta 2 O 5 , Bi 2 O 3 , MgO, CaO, SrO, BaO molecular weight: NWF1=[2×B 2 O 3 /M(B 2 O 3 )]+[SiO 2 /M(SiO 2 )]+[2× Al 2 O 3 /M(Al 2 O 3 )]; RE1=[2 ×La 2 O 3 /M(La 2 O 3 )]+[2×Gd 2 O 3 /M(Gd 2 O 3 )]+ [2×Y 2 O 3 /M(Y 2 O 3 )]+[2×Yb 2 O 3 /M(Yb 2 O 3 )]+[LaF 3 /M(LaF 3 )]+[GdF 3 /M (GdF 3 )]+[YF 3 /M(YF 3 )]+[YbF 3 /M(YbF 3 )]; HR1=[2×Nb 2 O 5 /M(Nb 2 O 5 )]+[TiO 2 /M (TiO 2 )]+[WO 3 /M(WO 3 )]+[2×Bi 2 O 3 /M(Bi 2 O 3 )]; D1={[2×Li 2 O/M (Li 2 O)]+[2×Na 2 O/M(Na 2 O)]+[2×K 2 O/M(K 2 O)]}×3+[ZnO/M(ZnO)]; L1=[20 ×Li 2 O/M(Li 2 O)]+[16×Na 2 O/M(Na 2 O)]+[8×K 2 O/M (K 2 O)]+[4×ZnO/M( ZnO)]+[MgO/M(MgO)]+[2×CaO/M(CaO)] +[2×SrO/M(SrO)]+[2×BaO/M(BaO)]+[2×B 2 O 3 /M(B 2 O 3 )]+[2×Nb 2 O 5 /M( Nb 2 O 5 )]+[TiO 2 /M(TiO 2 )]+[4×WO 3 /M(WO 3 )]+[8×Bi 2 O 3 /M(Bi 2 O 3 )]+[2 ×Ta 2 O 5 /M(Ta 2 O 5 )]-[2×SiO 2 /M(SiO 2 )]-[2×Al 2 O 3 /M(Al 2 O 3 )]-[2×ZrO 2 /M(ZrO 2 )]-[2×La 2 O 3 /M(La 2 O 3 )]-[2×Gd 2 O 3 /M(Gd 2 O 3 )]-[2×Y 2 O 3 / M(Y 2 O 3 )]-[2×Yb 2 O 3 /M(Yb 2 O 3 )]-[LaF 3 /M(LaF 3 )]-[GdF 3 /M(GdF 3 )]-[YF 3 /M(YF 3 )]-[YbF 3 /M(YbF 3 )]; the content of each of the above-mentioned glass components is a value represented by mass %.

另外，在上述式中，表示為三氧化二硼(B2 O3 )、二氧化矽(SiO2 )、三氧化二鋁(Al2 O3 )、三氧化二鑭(La2 O3 )、三氧化二釓(Gd2 O3 )、三氧化二釔(Y2 O3 )、三氧化二鐿(Yb2 O3 )、五氧化二鈮(Nb2 O5 )、二氧化鈦(TiO2 )、氧化鎢(WO3 )、三氧化二鉍(Bi2 O3 )、氧化鋰(Li2 O)、氧化鈉(Na2 O)、氧化鉀(K2 O)、氧化鋅(ZnO)、氧化鎂(MgO)、氧化鈣(CaO)、氧化鍶(SrO)、氧化鋇(BaO)、五氧化二鉭(Ta2 O5 )、二氧化鋯(ZrO2 )、氟化鑭(LaF3 )、氟化釓(GdF3 )、三氟化釔(YF3 )及三氟化鐿(YbF3 )的各玻璃成分的含量為以質量%表示的各玻璃成分的含有比例。不對NWF1、RE1、HR1、L1、D1附加質量%或%等表示百分率的符號，僅用數值來表示。在以下的記載中也一樣。In addition, in the above formula, it is represented by boron trioxide (B 2 O 3 ), silicon dioxide (SiO 2 ), aluminum oxide (Al 2 O 3 ), lanthanum trioxide (La 2 O 3 ), Yttrium trioxide (Gd 2 O 3 ), yttrium trioxide (Y 2 O 3 ), ytterbium trioxide (Yb 2 O 3 ), niobium pentoxide (Nb 2 O 5 ), titanium dioxide (TiO 2 ), Tungsten oxide (WO 3 ), bismuth trioxide (Bi 2 O 3 ), lithium oxide (Li 2 O), sodium oxide (Na 2 O), potassium oxide (K 2 O), zinc oxide (ZnO), magnesium oxide (MgO), calcium oxide (CaO), strontium oxide (SrO), barium oxide (BaO), tantalum pentoxide (Ta 2 O 5 ), zirconium dioxide (ZrO 2 ), lanthanum fluoride (LaF 3 ), fluorine The contents of the respective glass components of yttrium (GdF 3 ), yttrium trifluoride (YF 3 ), and ytterbium trifluoride (YbF 3 ) are the content ratios of the respective glass components expressed in mass %. No symbols representing percentages such as mass % or % are added to NWF1, RE1, HR1, L1, and D1, and only numerical values are used to represent them. The same applies to the following description.

在本實施形態中，基於以質量%表示的各玻璃成分的含量對本發明的光學玻璃進行說明。因此，以下只要沒有特別說明，各含量就以質量%來表示。In this embodiment, the optical glass of this invention is demonstrated based on the content of each glass component represented by mass %. Therefore, unless otherwise specified, each content is represented by mass %.

另外，在本說明書中，以質量%表示是指，對於以氧化物、氟化物表示的各玻璃成分，用質量百分率來表示將全部玻璃成分的合計含量設為100質量%時的各玻璃成分的含量。In addition, in this specification, the expression in mass % means that, with respect to each glass component represented by an oxide and a fluoride, the total content of all glass components is represented by mass percentage of each glass component when the total content of all glass components is 100 mass %. content.

像後面說明的那樣，有時在玻璃中添加少量三氧化二銻(Sb2 O3 )、二氧化錫(SnO2 )、二氧化鈰(CeO2 )作為澄清劑。但是，在本說明書中以質量%表示時，全部玻璃成分的合計含量中不包括Sb2 O3 、SnO2 及CeO2 的含量。即，玻璃成分中的Sb2 O3 、SnO2 、CeO2 的以質量%表示的各含量表示為，將Sb2 O3 、SnO2 及CeO2 以外的全部玻璃成分的合計含量設為100質量%的情況下的Sb2 O3 、SnO2 、CeO2 的各含量。在本說明書中將這樣的表示稱為外加。As described later, a small amount of antimony trioxide (Sb 2 O 3 ), tin dioxide (SnO 2 ), and ceria (CeO 2 ) may be added to glass as a clarifying agent. However, when it is represented by mass % in this specification, content of Sb2O3 , SnO2 , and CeO2 is not included in the total content of all glass components. That is, each content in mass % of Sb 2 O 3 , SnO 2 , and CeO 2 in the glass components is represented by the total content of all glass components other than Sb 2 O 3 , SnO 2 and CeO 2 being 100 mass Each content of Sb 2 O 3 , SnO 2 , and CeO 2 in the case of %. In this specification, such an expression is referred to as an addition.

此外，合計含量是指複數種玻璃成分的含量(也包括含量為0%的情況)的合計量。此外，質量比是指以質量%表示的玻璃成分的含量(也包括複數種成分的合計含量)彼此的比例(比)。In addition, the total content means the total amount of the content of a plurality of glass components (including the case where the content is 0%). In addition, the mass ratio means the ratio (ratio) of the content of the glass components (including the total content of a plurality of components) expressed in mass %.

以下，將B2 O3 的分子量設為M(B2 O3 )，將SiO2 的分子量設為M(SiO2 )，將Al2 O3 的分子量設為M(Al2 O3 )，將La2 O3 的分子量設為M(La2 O3 )，將Gd2 O3 的分子量設為M(Gd2 O3 )，將Y2 O3 的分子量設為M(Y2 O3 )，將Yb2 O3 的分子量設為M(Yb2 O3 )，將LaF3 的分子量設為M(LaF3 )，將GdF3 的分子量設為M(GdF3 )，將YF3 的分子量設為M(YF3 )，將YbF3 的分子量設為M(YbF3 )，將ZnO的分子量設為M(ZnO)，將Li2 O的分子量設為M(Li2 O)，將Na2 O的分子量設為M(Na2 O)，將K2 O的分子量設為M(K2 O)，將ZrO2 的分子量設為M(ZrO2 )，將Nb2 O5 的分子量設為M(Nb2 O5 )，將TiO2 的分子量設為M(TiO2 )，將WO3 的分子量設為M(WO3 )，將Ta2 O5 的分子量設為M(Ta2 O5 )，將Bi2 O3 的分子量設為M(Bi2 O3 )，將MgO的分子量設為M(MgO)，將CaO的分子量設為M(CaO)，將SrO的分子量設為M(SrO)，將BaO的分子量設為M(BaO)。Hereinafter, the molecular weight of B 2 O 3 is M(B 2 O 3 ), the molecular weight of SiO 2 is M(SiO 2 ), the molecular weight of Al 2 O 3 is M(Al 2 O 3 ), and the molecular weight of Al 2 O 3 is M(Al 2 O 3 ). Let the molecular weight of La 2 O 3 be M(La 2 O 3 ), the molecular weight of Gd 2 O 3 shall be M(Gd 2 O 3 ), and the molecular weight of Y 2 O 3 shall be M(Y 2 O 3 ), Let the molecular weight of Yb 2 O 3 be M(Yb 2 O 3 ), the molecular weight of LaF 3 shall be M(LaF 3 ), the molecular weight of GdF 3 shall be M(GdF 3 ), and the molecular weight of YF 3 shall be M(YF 3 ), the molecular weight of YbF 3 is M(YbF 3 ), the molecular weight of ZnO is M(ZnO), the molecular weight of Li 2 O is M(Li 2 O), and the molecular weight of Na 2 O is M(Li 2 O) The molecular weight is M(Na 2 O), the molecular weight of K 2 O is M(K 2 O), the molecular weight of ZrO 2 is M(ZrO 2 ), and the molecular weight of Nb 2 O 5 is M(Nb 2 O 5 ), let the molecular weight of TiO 2 be M(TiO 2 ), let the molecular weight of WO 3 be M(WO 3 ), let the molecular weight of Ta 2 O 5 be M(Ta 2 O 5 ), and let Bi The molecular weight of 2 O 3 is M(Bi 2 O 3 ), the molecular weight of MgO is M(MgO), the molecular weight of CaO is M(CaO), the molecular weight of SrO is M(SrO), and the molecular weight of BaO is M(SrO). The molecular weight of is set to M(BaO).

各氧化物的分子量是該氧化物的一個分子中包含的相當於陽離子的原子的數與該原子的原子量的積和該氧化物的一個分子中包含的氧(O)的數與氧的原子量的積的合計，相當於化學式量。此外，各氟化物的分子量是該氟化物的一個分子中包含的相當於陽離子的原子的數與該原子的原子量的積和該氟化物的一個分子中包含的氟(F)的數與氟的原子量的積的合計。而且，每1mol的分子的質量為在其分子量附上單位(g)的值。在表1中，將上述各氧化物、各氟化物的分子量表示到小數點後3位。例如，在以下的說明中只要使用表1所示的數值作為分子量即可。The molecular weight of each oxide is the product of the number of atoms corresponding to cations contained in one molecule of the oxide and the atomic weight of the atom, and the number of oxygen (O) contained in one molecule of the oxide and the atomic weight of oxygen. The total of the product is equivalent to the chemical formula quantity. In addition, the molecular weight of each fluoride is the product of the number of atoms corresponding to cations contained in one molecule of the fluoride and the atomic weight of the atom and the sum of the number of fluorine (F) contained in one molecule of the fluoride and the difference between fluorine and fluorine. The sum of the products of atomic weights. In addition, the mass per 1 mol of molecules is a value obtained by adding a unit (g) to the molecular weight. In Table 1, the molecular weights of the above-mentioned oxides and fluorides are shown to 3 decimal places. For example, in the following description, the numerical value shown in Table 1 may be used as the molecular weight.

[表1] M(B2 O3 ) 69.621 M(SiO2 ) 60.084 M(Al2 O3 ) 101.961 M(La2 O3 ) 325.809 M(Gd2 O3 ) 362.498 M(Y2 O3 ) 225.810 M(Yb2 O3 ) 394.084 M(ZnO) 81.389 M(Li2 O) 29.882 M(Na2 O) 61.979 M(K2 O) 94.196 M(ZrO2 ) 123.223 M(Nb2 O5 ) 265.810 M(TiO2 ) 79.882 M(WO3 ) 231.839 M(Ta2 O5 ) 441.893 M(Bi2 O3 ) 465.959 M(MgO) 40.304 M(CaO) 56.077 M(SrO) 81.389 M(BaO) 153.326 M(LaF3 ) 195.901 M(GdF3 ) 214.245 M(YF3 ) 145.901 M(YbF3 ) 230.050 [Table 1] M(B 2 O 3 ) 69.621 M(SiO 2 ) 60.084 M(Al 2 O 3 ) 101.961 M(La 2 O 3 ) 325.809 M(Gd 2 O 3 ) 362.498 M(Y 2 O 3 ) 225.810 M(Yb 2 O 3 ) 394.084 M(ZnO) 81.389 M(Li 2 O) 29.882 M(Na 2 O) 61.979 M(K 2 O) 94.196 M(ZrO 2 ) 123.223 M(Nb 2 O 5 ) 265.810 M(TiO 2 ) 79.882 M(WO 3 ) 231.839 M(Ta 2 O 5 ) 441.893 M(Bi 2 O 3 ) 465.959 M(MgO) 40.304 M(CaO) 56.077 M(SrO) 81.389 M(BaO) 153.326 M(LaF 3 ) 195.901 M(GdF 3 ) 214.245 M(YF 3 ) 145.901 M(YbF 3 ) 230.050

進而，在表2示出以氧化物或氟化物表示玻璃成分時的一個分子中包含的陽離子的個數。Furthermore, Table 2 shows the number of cations contained in one molecule when the glass component is represented by an oxide or a fluoride.

[表2] 玻璃成分 一個分子中包含的陽離子的個數 B2 O3 2 SiO2 1 Al2 O3 2 La2 O3 2 Gd2 O3 2 Y2 O3 2 Yb2 O3 2 ZnO 1 Li2 O 2 Na2 O 2 K2 O 2 ZrO2 1 Nb2 O5 2 TiO2 1 WO3 1 Ta2 O5 2 Bi2 O3 2 MgO 1 CaO 1 SrO 1 BaO 1 LaF3 1 GdF3 1 YF3 1 YbF3 1 [Table 2] glass composition The number of cations contained in a molecule B 2 O 3 2 SiO2 1 Al 2 O 3 2 La 2 O 3 2 Gd 2 O 3 2 Y 2 O 3 2 Yb 2 O 3 2 ZnO 1 Li 2 O 2 Na 2 O 2 K 2 O 2 ZrO 2 1 Nb 2 O 5 2 TiO 2 1 WO 3 1 Ta 2 O 5 2 Bi 2 O 3 2 MgO 1 CaO 1 SrO 1 BaO 1 LaF 3 1 GdF 3 1 YF 3 1 YbF 3 1

以下，對本實施形態的光學玻璃進行詳細說明。Hereinafter, the optical glass of this embodiment is demonstrated in detail.

在本實施形態的光學玻璃中，阿貝數(νd)為39.0以上、45.0以下，折射率(nd)與上述的阿貝數(νd)滿足下述式(1)。In the optical glass of the present embodiment, the Abbe number (νd) is 39.0 or more and 45.0 or less, and the refractive index (nd) and the above-mentioned Abbe number (νd) satisfy the following formula (1).

式(1) nd≥2.235-0.01×νd 在本實施形態的光學玻璃中，阿貝數(νd)的下限為39.0，較佳為39.5，更佳為40.0，進一步較佳為40.5。阿貝數(νd)的上限為45.0，較佳為44.5，更佳為44.0，進一步較佳為43.5。Formula 1) nd≥2.235-0.01×νd In the optical glass of the present embodiment, the lower limit of the Abbe number (νd) is 39.0, preferably 39.5, more preferably 40.0, further preferably 40.5. The upper limit of the Abbe number (νd) is 45.0, preferably 44.5, more preferably 44.0, and further preferably 43.5.

當阿貝數(νd)為39.0以上時，作為光學元件的材料對於校正色像差是有效的。此外，當阿貝數(νd)大於45.0時，如果不使折射率(nd)下降，則玻璃的熱穩定性會顯著下降，在製造玻璃的過程中容易失透。此外，藉由使折射率(nd)相對於阿貝數(νd)處於由式(1)決定的範圍內，從而能夠製成在光學設計上利用價值高的光學玻璃。折射率(nd)的上限根據玻璃的上述組成範圍自然而然地確定。When the Abbe number (νd) is 39.0 or more, it is effective as a material for the optical element to correct chromatic aberration. In addition, when the Abbe number (νd) is larger than 45.0, unless the refractive index (nd) is lowered, the thermal stability of the glass is significantly lowered, and devitrification is likely to occur during the production of the glass. In addition, by making the refractive index (nd) fall within the range determined by the formula (1) with respect to the Abbe number (νd), it is possible to produce an optical glass with high utility value in optical design. The upper limit of the refractive index (nd) is naturally determined according to the above-mentioned composition range of the glass.

在本實施形態的光學玻璃中，後述的NWF1、RE1、HR1意味著每100g玻璃所包含的特定陽離子的莫耳數的合計。在此，NWF1、RE1、HR1是關於本發明的光學玻璃中的特定的玻璃成分的含量的指標，不附加質量%或%等表示百分率的符號，僅用數值來表示。以下，以NWF1為例進行詳細說明。In the optical glass of the present embodiment, NWF1, RE1, and HR1 described later mean the total number of moles of specific cations contained in 100 g of glass. Here, NWF1, RE1, and HR1 are indicators of the content of a specific glass component in the optical glass of the present invention, and are only represented by numerical values without adding symbols such as mass % or % to represent percentages. Hereinafter, the NWF1 will be described in detail by taking NWF1 as an example.

上述NWF1用下述數學式1來表示。The above-mentioned NWF1 is represented by the following mathematical formula 1.

[數學式1]

Figure 02_image001
[Mathematical formula 1]
Figure 02_image001

在此，上述數學式1中的[B2 O3 /M(B2 O3 )]的分母為三氧化二硼(B2 O3 )的分子量，分子為三氧化二硼(B2 O3 )的以質量%表示的含量。Here, the denominator of [B 2 O 3 /M(B 2 O 3 )] in the above mathematical formula 1 is the molecular weight of diboron trioxide (B 2 O 3 ), and the numerator is diboron trioxide (B 2 O 3 ). ) in mass %.

關於分子，換言之，以質量%表示的三氧化二硼(B2 O3 )的含量是將每100g玻璃所包含的三氧化二硼(B2 O3 )的含量用質量(g)表示的含量。Regarding the molecule, in other words, the content of diboron trioxide (B 2 O 3 ) expressed in mass % is the content expressed by mass (g) of the content of diboron trioxide (B 2 O 3 ) contained in 100 g of glass .

因此，上述數學式1中的[B2 O3 /M(B2 O3 )]相當於每100g玻璃所包含的三氧化二硼(B2 O3 )的莫耳數。Therefore, [B 2 O 3 /M(B 2 O 3 )] in the above mathematical formula 1 corresponds to the number of moles of diboron trioxide (B 2 O 3 ) contained in 100 g of glass.

進而，上述[B2 O3 /M(B2 O3 )]乘以1個分子的三氧化二硼(B2 O3 )所包含的陽離子(B3+ )的個數(2)的[2×B2 O3 /M(B2 O3 )]相當於每100g玻璃所包含的硼離子(B3+ )的莫耳數。Furthermore, the above [B 2 O 3 /M(B 2 O 3 )] is obtained by multiplying the number (2) of cations (B 3+ ) contained in one molecule of diboron trioxide (B 2 O 3 ) by [ 2×B 2 O 3 /M(B 2 O 3 )] corresponds to the number of moles of boron ions (B 3+ ) contained in 100 g of glass.

另外，上述數學式1中的[SiO2 /M(SiO2 )]和[2×Al2 O3 /M(Al2 O3 )]也與[2×B2 O3 /M(B2 O3 )]的情況相同。In addition, [SiO 2 /M(SiO 2 )] and [2×Al 2 O 3 /M(Al 2 O 3 )] in the above mathematical formula 1 are also the same as [2×B 2 O 3 /M(B 2 O 3 )] is the same.

因此，NWF1為每100g玻璃所包含的硼離子(B3+ )、矽離子(Si4+ )及鋁離子(Al3+ )的各莫耳數的合計值。在此，NWF1是關於本發明的光學玻璃中的網絡形成成分的含量的指標，僅由數值來表示。Therefore, NWF1 is the total value of each molar number of boron ions (B 3+ ), silicon ions (Si 4+ ), and aluminum ions (Al 3+ ) contained in the glass per 100 g. Here, NWF1 is an index regarding the content of the network-forming component in the optical glass of the present invention, and is only represented by a numerical value.

此外，後述的HR1、RE1、R1也與NWF1的情況相同。In addition, HR1, RE1, and R1 to be described later are also the same as in the case of NWF1.

＜RE1/NWF1＞ 在本實施形態的光學玻璃中，NWF1像上述那樣定義。另外，B2 O3 、SiO2 、Al2 O3 作為玻璃的網絡形成成分而發揮功能。<RE1/NWF1> In the optical glass of this embodiment, NWF1 is defined as above. In addition, B 2 O 3 , SiO 2 , and Al 2 O 3 function as network-forming components of glass.

在本實施形態的光學玻璃中，RE1是將以質量%表示的高折射率低色散化成分La2 O3 、Gd2 O3 、Y2 O3 、Yb2 O3 、LaF3 、GdF3 、YF3 、YbF3 的各含量的各數值分別除以各氧化物、氟化物的分子量，再分別乘以各分子中包含的陽離子的個數的值的合計值(RE1=[2×La2 O3 /M(La2 O3 )]+[2×Gd2 O3 /M(Gd2 O3 )]+[2× Y2 O3 /M(Y2 O3 )]+[2×Yb2 O3 /M(Yb2 O3 )]+[LaF3 /M(LaF3 )]+[GdF3 /M(GdF3 )]+[YF3 /M(YF3 )]+[YbF3 /M(YbF3 )])。即，RE1是每100g玻璃所包含的La3+ 、Gd3+ 、Y3+ 及Yb3+ 的各莫耳數的合計值。在此，RE1是關於本發明的光學玻璃中的高折射率低色散化成分的含量的指標，僅用數值來表示。 In the optical glass of the present embodiment, RE1 is a combination of high refractive index and low dispersion components La2O3 , Gd2O3 , Y2O3 , Yb2O3 , LaF3 , GdF3 , Each value of each content of YF 3 and YbF 3 is divided by the molecular weight of each oxide and fluoride, respectively, and then multiplied by the total value of the number of cations contained in each molecule (RE1=[2×La 2 O 3 /M(La 2 O 3 )]+[2×Gd 2 O 3 /M(Gd 2 O 3 )]+[2× Y 2 O 3 /M(Y 2 O 3 )]+[2×Yb 2 O 3 /M(Yb 2 O 3 )]+[LaF 3 /M(LaF 3 )]+[GdF 3 /M(GdF 3 )]+[YF 3 /M(YF 3 )]+[YbF 3 /M (YbF 3 )]). That is, RE1 is the total value of each molar number of La 3+ , Gd 3+ , Y 3+ and Yb 3+ contained per 100 g of glass. Here, RE1 is an index regarding the content of the high-refractive-index and low-dispersion component in the optical glass of the present invention, and is only represented by numerical values.

當NWF1減小時，折射率上升。當RE1增大時，可在阿貝數不大幅減小的情況下使折射率上升。因此，藉由使比[RE1/NWF1]增大，從而能夠在維持低色散特性的同時使折射率上升。When NWF1 decreases, the refractive index increases. When RE1 is increased, the refractive index can be increased without greatly decreasing the Abbe number. Therefore, by increasing the ratio [RE1/NWF1], it is possible to increase the refractive index while maintaining the low dispersion characteristics.

為了得到所需的折射率(nd)、阿貝數(νd)，在本實施形態的光學玻璃中，比[RE1/NWF1]為0.35以上。In order to obtain the desired refractive index (nd) and Abbe's number (νd), in the optical glass of the present embodiment, the ratio [RE1/NWF1] is 0.35 or more.

進而，在本實施形態的光學玻璃中，比[RE1/NWF1]的下限較佳為0.36，進而依次更佳為0.37、0.38、0.39、0.40、0.41、0.42、0.43。Furthermore, in the optical glass of the present embodiment, the lower limit of the ratio [RE1/NWF1] is preferably 0.36, and more preferably 0.37, 0.38, 0.39, 0.40, 0.41, 0.42, and 0.43 in this order.

在本實施形態的光學玻璃中，藉由將比[RE1/ NWF1]的下限設為上述範圍，從而能夠使折射率(nd)和阿貝數(νd)成為所需的值。In the optical glass of the present embodiment, by setting the lower limit of the ratio [RE1/NWF1] to the above range, the refractive index (nd) and the Abbe number (νd) can be set to desired values.

當NWF1增大時，可改善玻璃的熱穩定性，在製造玻璃、成型玻璃時不易析出晶體。當RE1減小時，可改善玻璃的熱穩定性，在製造過程中不易析出晶體。When the NWF1 is increased, the thermal stability of the glass can be improved, and crystals are not easily precipitated during glass production and glass molding. When RE1 is reduced, the thermal stability of the glass can be improved, and crystals are not easily precipitated during the manufacturing process.

因此，為了改善玻璃的熱穩定性、得到不易析出晶體的玻璃，比[RE1/NWF1]的上限較佳為0.80，進而依次更佳為0.70、0.60、0.55、0.54、0.53、0.52、0.51。藉由將比[RE1/NWF1]的上限設為上述較佳的範圍，從而能夠進一步改善玻璃的熱穩定性。Therefore, in order to improve the thermal stability of the glass and obtain a glass in which crystals are not easily precipitated, the upper limit of the ratio [RE1/NWF1] is preferably 0.80, and more preferably 0.70, 0.60, 0.55, 0.54, 0.53, 0.52, and 0.51 in this order. By setting the upper limit of the ratio [RE1/NWF1] to the above-mentioned preferable range, the thermal stability of the glass can be further improved.

在本實施形態的光學玻璃中，從提高折射率的觀點出發，NWF1的上限較佳為0.80，進而依次更佳為0.75、0.72、0.70、0.69、0.68。此外，從改善玻璃的熱穩定性的觀點出發，NWF1的下限較佳為0.45，進而依次更佳為0.48、0.50、0.53、0.54、0.55。In the optical glass of the present embodiment, from the viewpoint of increasing the refractive index, the upper limit of NWF1 is preferably 0.80, and more preferably 0.75, 0.72, 0.70, 0.69, and 0.68 in this order. In addition, from the viewpoint of improving the thermal stability of the glass, the lower limit of NWF1 is preferably 0.45, and more preferably 0.48, 0.50, 0.53, 0.54, and 0.55 in this order.

在本實施形態的光學玻璃中，從改善玻璃的熱穩定性的觀點出發，RE1的上限較佳為0.37，更佳為0.35，進一步較佳為0.33，再進一步較佳為0.31。此外，從在不使阿貝數大幅降低的情況下提高折射率的觀點出發，RE1的下限較佳為0.20，更佳為0.22，進一步較佳為0.24，再進一步較佳為0.26。In the optical glass of the present embodiment, from the viewpoint of improving the thermal stability of the glass, the upper limit of RE1 is preferably 0.37, more preferably 0.35, still more preferably 0.33, and still more preferably 0.31. In addition, from the viewpoint of increasing the refractive index without significantly lowering the Abbe number, the lower limit of RE1 is preferably 0.20, more preferably 0.22, still more preferably 0.24, and still more preferably 0.26.

＜HR1/RE1＞ 如前所述，阿貝數(νd)為39.0以上、45.0以下的光學玻璃具有滿足式(1)的折射率在光學設計上意義很大。通常，當使玻璃的折射率增加時，阿貝數會減小、會高色散化。因此，要得到上述光學特性，重要的是在儘量抑制阿貝數(νd)的減小的同時提高折射率。<HR1/RE1> As described above, it is significant in optical design that the optical glass having an Abbe number (νd) of 39.0 or more and 45.0 or less has a refractive index satisfying the formula (1). Generally, when the refractive index of glass is increased, the Abbe number is decreased and the dispersion is increased. Therefore, in order to obtain the above-mentioned optical properties, it is important to increase the refractive index while suppressing the decrease in Abbe's number (νd) as much as possible.

稀土類氧化物和Nb2 O5 、TiO2 、WO3 及Bi2 O3 均具有使玻璃的折射率上升的作用，與稀土類氧化物相比，Nb2 O5 、TiO2 、WO3 及Bi2 O3 使阿貝數減小的作用(高色散化的作用)強。Rare earth oxides, Nb 2 O 5 , TiO 2 , WO 3 and Bi 2 O 3 all have the effect of increasing the refractive index of glass. Compared with rare earth oxides, Nb 2 O 5 , TiO 2 , WO 3 and Bi 2 O 3 has a strong effect of reducing the Abbe number (effect of high dispersion).

可是，在精密壓製成型中，如果玻璃與壓製成型模的模材料反應，玻璃表面的透明度就會下降，還會產生玻璃與壓製成型模熔著的問題。在精密壓製成型中，與壓製成型模的模材料反應的物質主要是玻璃成分中的在高溫下容易發生價數的變化的成分，即Nb2 O5 、TiO2 、WO3 、Bi2 O3 。另一方面，雖然稀土類氧化物與Nb2 O5 、TiO2 、WO3 、Bi2 O3 同樣具有使折射率上升的作用，但是與Nb2 O5 、TiO2 、WO3 、Bi2 O3 不同，在精密壓製成型時的高溫狀態下不易發生價數的變化，與模材料的反應性較低。因此，期望相對於稀土類氧化物的含量將成為玻璃與模材料的化學反應的主要原因的Nb2 O5 、TiO2 、WO3 、Bi2 O3 的含量抑制在一定量以下。However, in precision press molding, if the glass reacts with the mold material of the press mold, the transparency of the glass surface will decrease, and there will be a problem that the glass and the press mold are fused. In the precision press molding, the substances that react with the mold material of the press molding die are mainly components of the glass components that are prone to change in valence at high temperature, namely Nb 2 O 5 , TiO 2 , WO 3 , Bi 2 O 3 . . On the other hand, the rare earth oxides have the same action of raising the refractive index as Nb 2 O 5 , TiO 2 , WO 3 , and Bi 2 O 3 , but are different from those of Nb 2 O 5 , TiO 2 , WO 3 , and Bi 2 O . 3 is different, in the high temperature state during precision press molding, the valence change is not easy to occur, and the reactivity with the mold material is low. Therefore, the content of Nb 2 O 5 , TiO 2 , WO 3 , and Bi 2 O 3 , which are the main causes of the chemical reaction between the glass and the mold material, is desirably suppressed to a certain amount or less relative to the content of the rare earth oxide.

在本實施形態的光學玻璃中，HR1是將以質量%表示的高折射率高色散化成分Nb2 O5 、TiO2 、WO3 、Bi2 O3 的各含量的各數值分別除以各玻璃成分的分子量、再分別乘以各分子中包含的陽離子的個數的值的合計值(HR1=[2×Nb2 O5 /M (Nb2 O5 )]+[TiO2 /M(TiO2 )]+[WO3 /M(WO3 )]+[2×Bi2 O3 /M(Bi2 O3 )])。即，HR1是每100g玻璃所包含的Nb5+ 、Ti4+ 、W6+ 及Bi3+ 的各莫耳數的合計值。在此，HR1是關於本發明的光學玻璃中的高折射率高色散化成分的含量的指標，僅由數值表示。In the optical glass of the present embodiment, HR1 is obtained by dividing each numerical value of each content of the high refractive index and high dispersion components Nb 2 O 5 , TiO 2 , WO 3 , and Bi 2 O 3 represented by mass % by each glass. The total value of the molecular weight of the component and the value obtained by multiplying the number of cations contained in each molecule (HR1=[2×Nb 2 O 5 /M (Nb 2 O 5 )]+[TiO 2 /M (TiO 2 )]+[WO 3 /M(WO 3 )]+[2×Bi 2 O 3 /M(Bi 2 O 3 )]). That is, HR1 is the total value of each molar number of Nb 5+ , Ti 4+ , W 6+ and Bi 3+ contained in 100 g of glass. Here, HR1 is an index regarding the content of the high refractive index and high dispersion component in the optical glass of the present invention, and is only represented by numerical values.

藉由使HR1相對於RE1的比[HR1/RE1]減小，從而能夠抑制阿貝數的降低，進而能夠抑制精密壓製成型時的玻璃與模材料的反應，提高精密壓製成型的玻璃制光學元件的生產性。By reducing the ratio of HR1 to RE1 [HR1/RE1], the decrease in Abbe number can be suppressed, and the reaction between the glass and the mold material during precision press molding can be suppressed, and the precision press-molded glass optical element can be improved. productivity.

根據這樣的理由，在本實施形態的光學玻璃中，比[HR1/RE1]為0.33以下。For such reasons, in the optical glass of the present embodiment, the ratio [HR1/RE1] is 0.33 or less.

進而，在本實施形態的光學玻璃中，比[HR1/RE1]的上限較佳為0.32，進而依次更佳為0.31、0.30、0.29、0.28、0.27、0.25。Furthermore, in the optical glass of the present embodiment, the upper limit of the ratio [HR1/RE1] is preferably 0.32, and more preferably 0.31, 0.30, 0.29, 0.28, 0.27, and 0.25 in this order.

當比[HR1/RE1]減小時，示出玻璃的熱穩定性降低的傾向，示出玻璃化轉變溫度上升的傾向。此外，與HR1相比，RE1對增加折射率的貢獻更大，因此從製作折射率更高的玻璃的觀點出發，在上述的範圍內，較佳比[HR1/RE1]大。因此，從改善玻璃的熱穩定性、降低玻璃化轉變溫度的觀點出發，或者從進一步提高折射率的觀點出發，比[HR1/RE1]的下限較佳為0.04，進而依次更佳為0.08、0.10、0.11、0.13、0.15、0.16。When the ratio [HR1/RE1] decreases, the thermal stability of the glass tends to decrease, and the glass transition temperature tends to increase. In addition, since RE1 contributes more to the increase of the refractive index than HR1, it is preferable that the ratio [HR1/RE1] be larger than [HR1/RE1] in the above-mentioned range from the viewpoint of producing glass with a higher refractive index. Therefore, from the viewpoint of improving the thermal stability of the glass and lowering the glass transition temperature, or from the viewpoint of further increasing the refractive index, the lower limit of the ratio [HR1/RE1] is preferably 0.04, and more preferably 0.08 and 0.10 in this order. , 0.11, 0.13, 0.15, 0.16.

在本實施形態的光學玻璃中，從抑制阿貝數的減小、藉由精密壓製成型更穩定地製造高質量的光學元件的觀點出發，HR1的上限較佳為0.100，進而依次更佳為0.090、0.080、0.070、0.060。此外，從進一步提高折射率、進一步改善玻璃的熱穩定性的觀點出發，HR1的下限較佳為0.010，進而依次更佳為0.020、0.030、0.040。In the optical glass of the present embodiment, the upper limit of HR1 is preferably 0.100, and more preferably 0.090, from the viewpoint of suppressing the decrease in Abbe's number and stably producing a high-quality optical element by precision press molding , 0.080, 0.070, 0.060. In addition, from the viewpoint of further increasing the refractive index and further improving the thermal stability of the glass, the lower limit of HR1 is preferably 0.010, and more preferably 0.020, 0.030, and 0.040 in this order.

＜Nb2 O5 /(Nb2 O5 +Ta2 O5 )＞ 在本實施形態的光學玻璃中，Nb2 O5 的含量相對於Nb2 O5 和Ta2 O5 的合計含量的質量比[Nb2 O5 /(Nb2 O5 +Ta2 O5 )]為2/3以上。即，本實施形態的光學玻璃包含Nb2 O5 ，且將Nb2 O5 的含量設為Ta2 O5 的含量的2倍以上。<Nb 2 O 5 /(Nb 2 O 5 +Ta 2 O 5 )> In the optical glass of the present embodiment, the mass ratio of the content of Nb 2 O 5 to the total content of Nb 2 O 5 and Ta 2 O 5 [Nb 2 O 5 /(Nb 2 O 5 +Ta 2 O 5 )] is 2/3 or more. That is, the optical glass of the present embodiment contains Nb 2 O 5 , and the content of Nb 2 O 5 is set to be twice or more the content of Ta 2 O 5 .

進而，在本實施形態的光學玻璃中，質量比[Nb2 O5 / (Nb2 O5 +Ta2 O5 )]的下限較佳為0.67，進而依次更佳為0.70、0.80、0.90、0.95、0.98、0.99。此外，質量比[Nb2 O5 /(Nb2 O5 +Ta2 O5 )]的上限較佳為1.00。Furthermore, in the optical glass of the present embodiment, the lower limit of the mass ratio [Nb 2 O 5 /(Nb 2 O 5 +Ta 2 O 5 )] is preferably 0.67, and more preferably 0.70, 0.80, 0.90, and 0.95 in this order. , 0.98, 0.99. Further, the upper limit of the mass ratio [Nb 2 O 5 /(Nb 2 O 5 +Ta 2 O 5 )] is preferably 1.00.

藉由將質量比[Nb2 O5 /(Nb2 O5 +Ta2 O5 )]的下限設為上述範圍，從而能夠抑制折射率的降低、維持玻璃的熱穩定性。進而，藉由將質量比[Nb2 O5 /(Nb2 O5 +Ta2 O5 )]的下限設為上述範圍，從而還能夠相對於Nb2 O5 的含量使Ta2 O5 的含量相對地減少、削減非常昂貴的Ta的使用量。By setting the lower limit of the mass ratio [Nb 2 O 5 /(Nb 2 O 5 +Ta 2 O 5 )] to the above range, it is possible to suppress a decrease in the refractive index and maintain the thermal stability of the glass. Furthermore, by setting the lower limit of the mass ratio [Nb 2 O 5 /(Nb 2 O 5 +Ta 2 O 5 )] to the above range, the content of Ta 2 O 5 can also be adjusted to the content of Nb 2 O 5 Relatively reduce and reduce the usage of very expensive Ta.

＜RE1/D1＞ 通常，適合於精密壓製成型的具有低溫軟化性的玻璃含有具有使玻璃化轉變溫度(Tg)降低的作用的Li2 O、Na2 O、K2 O或ZnO的任一種以上。特別是，在這樣的玻璃中，使玻璃化轉變溫度(Tg)降低的作用強的Li2 O和ZnO的含量多。但是，這些玻璃成分在製造玻璃的過程中容易從熔融玻璃揮發。<RE1/D1> Generally, glass with low-temperature softening properties suitable for precision press molding contains any one or more of Li 2 O, Na 2 O, K 2 O, or ZnO, which has the effect of lowering the glass transition temperature (Tg). . In particular, in such glass, there are many contents of Li 2 O and ZnO, which have a strong effect of lowering the glass transition temperature (Tg). However, these glass components are easily volatilized from molten glass in the process of producing glass.

當特定的玻璃成分即易揮發的玻璃成分從熔融玻璃選擇性地揮發時，玻璃的組成比會改變，折射率(nd)、阿貝數(νd)等特性不能成為所需的值。其結果是，難以穩定地生產具有所需的特性的玻璃。此外，如果在將熔融玻璃成型時特定的玻璃成分從高溫的玻璃表面揮發，則會在玻璃表面生成被稱為條紋的光學不均質部。在要求高均質性的光學玻璃中，產生這樣的條紋不是較佳的。When a specific glass component, ie, a volatile glass component, is selectively volatilized from the molten glass, the composition ratio of the glass changes, and properties such as the refractive index (nd) and Abbe's number (νd) cannot be set to desired values. As a result, it is difficult to stably produce glass having desired properties. Moreover, when a specific glass component volatilizes from a high temperature glass surface when a molten glass is shape|molded, the optical inhomogeneity part called streak will generate|occur|produce on the glass surface. In optical glasses requiring high homogeneity, it is not preferable to generate such fringes.

本申請的發明人藉由調查發現，熔融玻璃的揮發性依賴於易揮發的Li2 O、Na2 O、K2 O及ZnO的含量與不易揮發的La2 O3 、Gd2 O3 、Y2 O3 及Yb2 O3 的稀土類氧化物的含量的比。The inventors of the present application found through investigation that the volatility of molten glass depends on the contents of Li 2 O, Na 2 O, K 2 O, and ZnO, which are volatile, and La 2 O 3 , Gd 2 O 3 , and Y which are not volatile. The content ratio of rare earth oxides of 2 O 3 and Yb 2 O 3 .

在本實施形態的光學玻璃中，D1是將以質量%表示的Li2 O、Na2 O及K2 O的各含量的數值分別除以各玻璃成分的分子量，再分別乘以各分子中包含的陽離子的個數和3的值與將以質量%表示的ZnO的含量的數值除以分子量、再乘以分子中包含的陽離子的個數的值的合計值(D1=[2×Li2 O/M(Li2 O)] ×3+[2×Na2 O/M(Na2 O)]×3+[2×K2 O/M(K2 O)]×3+[ZnO/M(ZnO)])。乘以3是因為Li2 O、Na2 O及K2 O比ZnO易揮發。即，D1能夠表示為D1={[2×Li2 O/M(Li2 O)]+[2×Na2 O/M(Na2 O)]+[2× K2 O/M(K2 O)]}×3+[ZnO/M(ZnO)]。D1是關於本發明的光學玻璃中的揮發性成分的含量的指標，僅由數值表示。In the optical glass of the present embodiment, D1 is obtained by dividing the numerical value of each content of Li 2 O, Na 2 O and K 2 O expressed in mass % by the molecular weight of each glass component, and then multiplying by the amount contained in each molecule. The total value of the number of cations and the value of 3 and the value of the ZnO content expressed in mass % divided by the molecular weight and multiplied by the number of cations contained in the molecule (D1=[2×Li 2 O /M(Li 2 O)] ×3+[2×Na 2 O/M(Na 2 O)]×3+[2×K 2 O/M(K 2 O)]×3+[ZnO/M( ZnO)]). Multiplying by 3 is because Li 2 O, Na 2 O and K 2 O are more volatile than ZnO. That is, D1 can be expressed as D1={[2×Li 2 O/M(Li 2 O)]+[2×Na 2 O/M(Na 2 O)]+[2×K 2 O/M(K 2 O)]}×3+[ZnO/M(ZnO)]. D1 is an index regarding the content of the volatile component in the optical glass of the present invention, and is only represented by a numerical value.

D1是將促進熔融玻璃的揮發的因數數值化的值。另一方面，RE1是將抑制熔融玻璃的揮發的因數數值化的值。即，藉由使RE1相對於D1的比[RE1/D1]增大，從而能夠抑制熔融玻璃的揮發。D1 is a numerical value of a factor that promotes volatilization of molten glass. On the other hand, RE1 is a numerical value of the factor which suppresses volatilization of molten glass. That is, by increasing the ratio [RE1/D1] of RE1 to D1, volatilization of the molten glass can be suppressed.

像這樣，比[RE1/D1]是表示熔融玻璃即玻璃熔液的揮發性的指標。藉由將比[RE1/D1]設為0.90以上，從而能夠抑制熔融玻璃的揮發。其結果是，能夠穩定地生產具有所需的特性的光學玻璃。此外，還能夠保持玻璃的高均質性。因此，在本實施形態的光學玻璃中，比[RE1/D1]為0.90以上。In this way, the ratio [RE1/D1] is an index showing the volatility of molten glass, that is, molten glass. By making ratio [RE1/D1] 0.90 or more, volatilization of molten glass can be suppressed. As a result, optical glass having desired properties can be stably produced. In addition, the high homogeneity of the glass can be maintained. Therefore, in the optical glass of this embodiment, the ratio [RE1/D1] is 0.90 or more.

進而，從抑制熔融玻璃的揮發的觀點出發，在本實施形態的光學玻璃中，比[RE1/D1]的下限較佳為0.95，進而依次更佳為0.98、1.00、1.05、1.10、1.12、1.13。Furthermore, from the viewpoint of suppressing volatilization of the molten glass, in the optical glass of the present embodiment, the lower limit of the ratio [RE1/D1] is preferably 0.95, and more preferably 0.98, 1.00, 1.05, 1.10, 1.12, and 1.13 in this order. .

另一方面，當比[RE1/D1]減小時，玻璃化轉變溫度(Tg)會降低，精密壓製成型時的玻璃的溫度會降低。其結果是，在精密壓製成型時不易發生玻璃與壓製成型模的反應，容易維持壓製成型後的玻璃表面的透明性，容易抑制玻璃與壓製成型模的熔著。從這樣的觀點出發，比[RE1/D1]的上限較佳為2.5，進而依次更佳為2.3、2.2、2.15、2.10、2.08、2.07。On the other hand, when the ratio [RE1/D1] decreases, the glass transition temperature (Tg) decreases, and the temperature of the glass during precision press molding decreases. As a result, the reaction between the glass and the press-molding mold is less likely to occur during precision press-molding, the transparency of the glass surface after press-molding is easily maintained, and fusion of the glass and the press-molding mold is easily suppressed. From such a viewpoint, the upper limit of the ratio [RE1/D1] is preferably 2.5, and more preferably 2.3, 2.2, 2.15, 2.10, 2.08, and 2.07 in this order.

從抑制熔融玻璃的揮發的觀點出發，在本實施形態的光學玻璃中，D1的上限較佳為0.33，進而依次更佳為0.30、0.28、0.26、0.25。另一方面，從降低玻璃化轉變溫度的觀點出發，D1的下限較佳為0.05，進而依次更佳為0.08、0.10、0.12、0.13。From the viewpoint of suppressing volatilization of the molten glass, in the optical glass of the present embodiment, the upper limit of D1 is preferably 0.33, and more preferably 0.30, 0.28, 0.26, and 0.25 in this order. On the other hand, from the viewpoint of lowering the glass transition temperature, the lower limit of D1 is preferably 0.05, and more preferably 0.08, 0.10, 0.12, and 0.13 in this order.

＜L1/(NWF1+RE1)＞ 將玻璃成分大致分為具有使玻璃化轉變溫度(Tg)相對降低的作用的成分和具有使玻璃化轉變溫度(Tg)相對上升的作用的成分。具有使玻璃化轉變溫度(Tg)相對降低的作用的成分主要是Li2 O、Na2 O、K2 O、ZnO、MgO、CaO、SrO、BaO、B2 O3 、Nb2 O5 、TiO2 、WO3 、Bi2 O3 、Ta2 O5 。另一方面，相對於上述玻璃成分，具有使玻璃化轉變溫度(Tg)相對上升的作用的成分主要是SiO2 、Al2 O3 、ZrO2 、La2 O3 、Gd2 O3 、Y2 O3 、Yb2 O3 、LaF3 、GdF3 、YF3 、YbF3 。<L1/(NWF1+RE1)> The glass components are roughly classified into those having an action of relatively lowering the glass transition temperature (Tg) and those having an action of relatively increasing the glass transition temperature (Tg). The components having the effect of relatively lowering the glass transition temperature (Tg) are mainly Li 2 O, Na 2 O, K 2 O, ZnO, MgO, CaO, SrO, BaO, B 2 O 3 , Nb 2 O 5 , and TiO 2 , WO 3 , Bi 2 O 3 , Ta 2 O 5 . On the other hand, the components having the effect of relatively increasing the glass transition temperature (Tg) with respect to the above-mentioned glass components are mainly SiO 2 , Al 2 O 3 , ZrO 2 , La 2 O 3 , Gd 2 O 3 , and Y 2 O 3 , Yb 2 O 3 , LaF 3 , GdF 3 , YF 3 , YbF 3 .

本申請發明人進行研究的結果發現，L1相對於NWF1和RE1的合計值的比[L1/(NWF1+RE1)]與玻璃化轉變溫度(Tg)之間存在相關關係，其中，L1是將以質量%表示的上述玻璃成分的各含量的數值分別除以各玻璃成分的分子量，再分別乘以各分子中包含的陽離子的個數，進而作為係數分別乘以各玻璃成分對玻璃化轉變溫度(Tg)的影響度的值的合計值。在表3示出表示上述玻璃成分對玻璃化轉變溫度(Tg)的影響度的係數。As a result of research conducted by the inventors of the present application, it was found that there is a correlation between the ratio of L1 to the total value of NWF1 and RE1 [L1/(NWF1+RE1)] and the glass transition temperature (Tg), where L1 is a The numerical value of each content of the above-mentioned glass components expressed in mass % is divided by the molecular weight of each glass component, and then multiplied by the number of cations contained in each molecule, and further multiplied by the effect of each glass component on the glass transition temperature ( The total value of the value of the degree of influence of Tg). Table 3 shows the coefficients showing the degree of influence of the above-mentioned glass components on the glass transition temperature (Tg).

[表3] 玻璃成分 係數 玻璃成分 係數 玻璃成分 係數 Li2 O +10 SiO2 -2 Gd2 O3 -1 Na2 O +8 Al2 O3 -1 Y2 O3 -1 K2 O +4 Nb2 O5 +1 Yb2 O3 -1 ZnO +4 TiO2 +1 LaF3 -1 MgO +1 WO3 +4 GdF3 -1 CaO +2 Bi2 O3 +4 YF3 -1 SrO +2 Ta2 O5 +1 YbF3 -1 BaO +2 ZrO2 -2     B2 O3 +1 La2 O3 -1     [table 3] glass composition coefficient glass composition coefficient glass composition coefficient Li 2 O +10 SiO2 -2 Gd 2 O 3 -1 Na 2 O +8 Al 2 O 3 -1 Y 2 O 3 -1 K 2 O +4 Nb 2 O 5 +1 Yb 2 O 3 -1 ZnO +4 TiO 2 +1 LaF 3 -1 MgO +1 WO 3 +4 GdF 3 -1 CaO +2 Bi 2 O 3 +4 YF 3 -1 SrO +2 Ta 2 O 5 +1 YbF 3 -1 BaO +2 ZrO 2 -2 B 2 O 3 +1 La 2 O 3 -1

這樣的L1能夠表示為L1=[10×2×Li2 O/M(Li2 O)]+ [8×2×Na2 O/M(Na2 O)]+[4×2×K2 O/M(K2 O)]+[4×1×ZnO/M(ZnO)]+[1×1×MgO/M(MgO)]+[2×1×CaO/M(CaO)]+[2×1×SrO/M(SrO)]+[2×1×BaO/M(BaO)]+[1×2×B2 O3 /M(B2 O3 )]+[1×2×Nb2 O5 /M(Nb2 O5 )]+[1×1×TiO2 /M(TiO2 )]+[4×1×WO3 /M(WO3 )]+[4×2×Bi2 O3 /M(Bi2 O3 )]+[1×2×Ta2 O5 /M(Ta2 O5 )]+[-2×1×SiO2 /M(SiO2 )]+[-1×2×Al2 O3 /M(Al2 O3 )]+[-2×1×ZrO2 /M(ZrO2 )]+[-1×2×La2 O3 /M(La2 O3 )]+[-1×2×Gd2 O3 /M(Gd2 O3 )]+[-1×2×Y2 O3 /M(Y2 O3 )]+[-1×2×Yb2 O3 /M(Yb2 O3 )]+[-1×1×LaF3 /M(LaF3 )]+[-1×1×GdF3 /M(GdF3 )]+[-1×1×YF3 /M(YF3 )]+[-1×1×YbF3 /M(YbF3 )]。Such L1 can be expressed as L1=[10×2×Li 2 O/M(Li 2 O)]+[8×2×Na 2 O/M(Na 2 O)]+[4×2×K 2 O /M(K 2 O)]+[4×1×ZnO/M(ZnO)]+[1×1×MgO/M(MgO)]+[2×1×CaO/M(CaO)]+[2 ×1×SrO/M(SrO)]+[2×1×BaO/M(BaO)]+[1×2×B 2 O 3 /M(B 2 O 3 )]+[1×2×Nb 2 O 5 /M(Nb 2 O 5 )]+[1×1×TiO 2 /M(TiO 2 )]+[4×1×WO 3 /M(WO 3 )]+[4×2×Bi 2 O 3 /M(Bi 2 O 3 )]+[1×2×Ta 2 O 5 /M(Ta 2 O 5 )]+[−2×1×SiO 2 /M(SiO 2 )]+[−1× 2×Al 2 O 3 /M(Al 2 O 3 )]+[−2×1×ZrO 2 /M(ZrO 2 )]+[−1×2×La 2 O 3 /M(La 2 O 3 ) ]+[−1×2×Gd 2 O 3 /M(Gd 2 O 3 )]+[−1×2×Y 2 O 3 /M(Y 2 O 3 )]+[−1×2×Yb 2 O 3 /M(Yb 2 O 3 )]+[−1×1×LaF 3 /M(LaF 3 )]+[−1×1×GdF 3 /M(GdF 3 )]+[−1×1× YF 3 /M(YF 3 )]+[−1×1×YbF 3 /M(YbF 3 )].

即，值L1能夠表示為L1=[20×Li2 O/M(Li2 O)]+ [16×Na2 O/M(Na2 O)]+[8×K2 O/M(K2 O)]+[4×ZnO/M(ZnO)]+[MgO/M(MgO)]+[2×CaO/M(CaO)]+[2×SrO/M(SrO)]+[2×BaO/M(BaO)]+[2×B2 O3 /M(B2 O3 )]+[2×Nb2 O5 /M(Nb2 O5 )]+[TiO2 /M(TiO2 )]+[4×WO3 /M(WO3 )]+[8×Bi2 O3 /M(Bi2 O3 )]+[2×Ta2 O5 /M(Ta2 O5 )]-[2×SiO2 /M(SiO2 )]-[2×Al2 O3 /M(Al2 O3 )]-[2×ZrO2 /M(ZrO2 )]-[2×La2 O3 /M(La2 O3 )]-[2×Gd2 O3 /M(Gd2 O3 )]-[2×Y2 O3 /M(Y2 O3 )]-[2×Yb2 O3 /M(Yb2 O3 )]-[LaF3 /M(LaF3 )]-[GdF3 /M(GdF3 )]-[YF3 /M(YF3 )]-[YbF3 /M(YbF3 )]。That is, the value L1 can be expressed as L1=[20×Li 2 O/M(Li 2 O)]+[16×Na 2 O/M(Na 2 O)]+[8×K 2 O/M(K 2 O)]+[4×ZnO/M(ZnO)]+[MgO/M(MgO)]+[2×CaO/M(CaO)]+[2×SrO/M(SrO)]+[2×BaO /M(BaO)]+[2×B 2 O 3 /M(B 2 O 3 )]+[2×Nb 2 O 5 /M(Nb 2 O 5 )]+[TiO 2 /M(TiO 2 ) ]+[4×WO 3 /M(WO 3 )]+[8×Bi 2 O 3 /M(Bi 2 O 3 )]+[2×Ta 2 O 5 /M(Ta 2 O 5 )]-[ 2×SiO 2 /M(SiO 2 )]-[2×Al 2 O 3 /M(Al 2 O 3 )]-[2×ZrO 2 /M(ZrO 2 )]-[2×La 2 O 3 / M(La 2 O 3 )]-[2×Gd 2 O 3 /M(Gd 2 O 3 )]-[2×Y 2 O 3 /M(Y 2 O 3 )]-[2×Yb 2 O 3 /M(Yb 2 O 3 )]-[LaF 3 /M(LaF 3 )]-[GdF 3 /M(GdF 3 )]-[YF 3 /M(YF 3 )]-[YbF 3 /M(YbF 3 )].

L1是關於本發明的光學玻璃中影響玻璃化轉變溫度(Tg)的成分的含量的指標，僅由數值表示。L1 is an index regarding the content of the component affecting the glass transition temperature (Tg) in the optical glass of the present invention, and is only represented by a numerical value.

圖1是將橫軸設為L1相對於NWF1和RE1的合計值的比[L1/(NWF1+RE1)]及將縱軸設為玻璃化轉變溫度(Tg)，對公知的玻璃繪製了比[L1/(NWF1+RE1)]與玻璃化轉變溫度(Tg)的圖，其中，NWF1對應於玻璃成分中的網絡形成成分，RE1對應於稀土類氧化物及稀土類氟化物。從圖1可清楚地看出，點基本分佈在直線上，可知比[L1/(NWF1+RE1)]與玻璃化轉變溫度(Tg)存在相關關係。Fig. 1 plots the ratio [L1/(NWF1+RE1)] of L1 to the total value of NWF1 and RE1 on the horizontal axis and the glass transition temperature (Tg) on the vertical axis for a known glass [ L1/(NWF1+RE1)] vs. glass transition temperature (Tg), where NWF1 corresponds to the network-forming component in the glass component, and RE1 corresponds to rare earth oxides and rare earth fluorides. It can be clearly seen from Figure 1 that the points are basically distributed on a straight line, and it can be seen that there is a correlation between the ratio [L1/(NWF1+RE1)] and the glass transition temperature (Tg).

即，隨著比[L1/(NWF1+RE1)]的增加，玻璃化轉變溫度(Tg)降低，隨著比[L1/(NWF1+RE1)]的減小，玻璃化轉變溫度(Tg)上升。That is, as the ratio [L1/(NWF1+RE1)] increases, the glass transition temperature (Tg) decreases, and as the ratio [L1/(NWF1+RE1)] decreases, the glass transition temperature (Tg) increases .

像這樣，藉由使比[L1/(NWF1+RE1)]增加，從而能夠使玻璃化轉變溫度(Tg)降低，能夠提供適合於精密壓製成型的玻璃，即，能夠提供具有低溫軟化性的玻璃。此外，藉由使比[L1/(NWF1+RE1)]增加，從而能夠改善玻璃的熔融性，即，玻璃原料不會產生熔融殘留，能夠提供均質的玻璃。In this way, by increasing the ratio [L1/(NWF1+RE1)], the glass transition temperature (Tg) can be lowered, and glass suitable for precision press molding, that is, glass having low-temperature softening properties can be provided. . In addition, by increasing the ratio [L1/(NWF1+RE1)], the meltability of the glass can be improved, that is, the glass raw material can be provided with a homogeneous glass without remaining melted.

為了得到具有低溫軟化性和良好的熔融性的光學玻璃，在本實施形態的光學玻璃中，比[L1/(NWF1+RE1)]為0.78以上。In order to obtain the optical glass which has low-temperature softening property and favorable meltability, in the optical glass of this embodiment, the ratio [L1/(NWF1+RE1)] is 0.78 or more.

進而，在本實施形態的光學玻璃中，比[L1/ (NWF1+RE1)]的下限較佳為0.80，進而依次更佳為0.85、0.90、0.91、0.92、0.95、1.00、1.05。Furthermore, in the optical glass of the present embodiment, the lower limit of the ratio [L1/(NWF1+RE1)] is preferably 0.80, and more preferably 0.85, 0.90, 0.91, 0.92, 0.95, 1.00, and 1.05 in this order.

藉由將比[L1/(NWF1+RE1)]的下限設為上述範圍，從而能夠得到適合於精密壓製成型的低溫軟化性，並且能夠改善玻璃的熔融性。當比[L1/(NWF1+RE1)]過大時，示出玻璃的熱穩定性降低的傾向，示出折射率降低的傾向。從維持所需的折射率和熱穩定性的觀點出發，比[L1/(NWF1+RE1)]的上限較佳為2，進而依次更佳為1.8、1.6、1.5。By setting the lower limit of the ratio [L1/(NWF1+RE1)] to the above range, low-temperature softening properties suitable for precision press molding can be obtained, and the meltability of the glass can be improved. When the ratio [L1/(NWF1+RE1)] is too large, the thermal stability of the glass tends to decrease, and the refractive index tends to decrease. From the viewpoint of maintaining the desired refractive index and thermal stability, the upper limit of the ratio [L1/(NWF1+RE1)] is preferably 2, and more preferably 1.8, 1.6, and 1.5 in this order.

＜R1/NWF1＞ 在本實施形態的光學玻璃中，R1是將以質量%表示的鹼土類金屬氧化物MgO、CaO、SrO及BaO的各含量的數值分別除以各玻璃成分的分子量的值的合計值(R1=[MgO/M(MgO)]+ [CaO/M(CaO)]+[SrO/M(SrO)]+[BaO/M(BaO)])。即，R1是每100g玻璃所包含的Mg2+ 、Ca2+ 、Sr2+ 及Ba2+ 的各莫耳數的合計值。R1是關於本發明的光學玻璃中的鹼土類金屬氧化物的含量的指標，僅由數值表示。<R1/NWF1> In the optical glass of the present embodiment, R1 is a value obtained by dividing the numerical value of each content of the alkaline earth metal oxides MgO, CaO, SrO, and BaO expressed in mass % by the molecular weight of each glass component. Total value (R1=[MgO/M(MgO)]+[CaO/M(CaO)]+[SrO/M(SrO)]+[BaO/M(BaO)]). That is, R1 is the total value of each molar number of Mg 2+ , Ca 2+ , Sr 2+ and Ba 2+ contained in 100 g of glass. R1 is an index regarding the content of the alkaline earth metal oxide in the optical glass of the present invention, and is only represented by a numerical value.

將網絡形成成分B2 O3 、SiO2 、Al2 O3 與鹼土類金屬氧化物MgO、CaO、SrO、BaO相比較，網絡形成成分比鹼土類金屬氧化物抑制阿貝數的減小的作用更大。Comparing the network-forming components B 2 O 3 , SiO 2 , and Al 2 O 3 with the alkaline earth metal oxides MgO, CaO, SrO, and BaO, the network-forming components inhibit the decrease in Abbe number compared with the alkaline earth metal oxides bigger.

因此，R1相對於NWF1的比[R1/NWF1]的上限較佳為0.30，進而依次更佳為0.25、0.20、0.19、0.15、0.10、0.05、0.02。此外，比[R1/NWF1]的下限較佳為0。另外，比[R1/NWF1]也可以為0。Therefore, the upper limit of the ratio [R1/NWF1] of R1 to NWF1 is preferably 0.30, and more preferably 0.25, 0.20, 0.19, 0.15, 0.10, 0.05, and 0.02 in this order. Further, the lower limit of the ratio [R1/NWF1] is preferably 0. In addition, the ratio [R1/NWF1] may be 0.

藉由將比[R1/NWF1]的上限設為上述範圍，從而能夠抑制阿貝數的減小。By setting the upper limit of the ratio [R1/NWF1] to the above range, it is possible to suppress a decrease in the Abbe number.

＜玻璃組成＞ 以下，對玻璃組成進行詳細說明。另外，只要沒有特別說明，各種玻璃成分的含量等就以質量%表示。另外，合計含量是複數種玻璃成分的含量的合計量，也包括各含量為0%的情況。＜Glass composition＞ Hereinafter, the glass composition will be described in detail. In addition, unless otherwise specified, content of various glass components, etc. are shown in mass %. In addition, the total content is the total amount of the content of a plurality of glass components, and the case where each content is 0% is also included.

在本實施形態的光學玻璃中，B2 O3 的含量的上限較佳為32%，進而依次更佳為30%、28%、26%、25%、24%。此外，B2 O3 的含量的下限較佳為10%，進而依次更佳為13%、14%、15%、16%。In the optical glass of the present embodiment, the upper limit of the content of B 2 O 3 is preferably 32%, and more preferably 30%, 28%, 26%, 25%, and 24% in this order. In addition, the lower limit of the content of B 2 O 3 is preferably 10%, and more preferably 13%, 14%, 15%, and 16% in this order.

B2 O3 為玻璃的網絡形成成分，具有改善玻璃的熔融性並且抑制阿貝數的減小的作用。此外，與SiO2 相比不易使玻璃化轉變溫度(Tg)上升。當B2 O3 的含量少時，有玻璃的熱穩定性和熔融性降低的傾向。另一方面，當B2 O3 的含量多時，有折射率(nd)、化學耐久性降低的傾向。因此，從改善玻璃的熱穩定性、熔融性及成型性等的觀點出發，較佳B2 O3 的含量的下限為上述範圍。另一方面，從在得到所需的折射率的同時良好地維持化學耐久性的觀點出發，B2 O3 的含量的上限較佳為上述範圍。B 2 O 3 is a network-forming component of the glass, and has the effect of improving the meltability of the glass and suppressing the decrease in the Abbe number. Moreover, it is difficult to raise a glass transition temperature (Tg) compared with SiO2 . When the content of B 2 O 3 is small, the thermal stability and meltability of the glass tend to decrease. On the other hand, when the content of B 2 O 3 is large, the refractive index (nd) and chemical durability tend to decrease. Therefore, from the viewpoint of improving the thermal stability, meltability, moldability, etc. of the glass, the lower limit of the content of B 2 O 3 is preferably the above-mentioned range. On the other hand, the upper limit of the content of B 2 O 3 is preferably the above-mentioned range from the viewpoint of obtaining a desired refractive index while maintaining good chemical durability.

在本實施形態的光學玻璃中，SiO2 的含量的上限較佳為10%，進而依次更佳為8%、7%、6%、5%、4%、3%。此外，SiO2 的含量的下限較佳為0%。另外，SiO2 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of SiO 2 is preferably 10%, and more preferably 8%, 7%, 6%, 5%, 4%, and 3% in this order. Further, the lower limit of the content of SiO 2 is preferably 0%. In addition, the content of SiO 2 may be 0%.

SiO2 為玻璃的網絡形成成分，具有改善玻璃的化學耐久性、耐候性、提高熔融玻璃的黏性、使熔融玻璃容易成型為玻璃的作用。當SiO2 的含量少時，有玻璃的熱穩定性、化學耐久性降低的傾向。另一方面，當SiO2 的含量多時，有玻璃的熔融性、低溫軟化性降低的傾向，即，有玻璃化轉變溫度上升、玻璃原料產生熔融殘留的傾向。因此，從改善玻璃的熔融性、低溫軟化性的觀點出發，SiO2 的含量的上限較佳為上述範圍。SiO 2 is a network forming component of glass, which has the functions of improving the chemical durability and weather resistance of glass, increasing the viscosity of molten glass, and making it easy to form molten glass into glass. When the content of SiO 2 is small, the thermal stability and chemical durability of the glass tend to decrease. On the other hand, when the content of SiO 2 is large, the meltability and low-temperature softening properties of the glass tend to decrease, that is, the glass transition temperature tends to rise, and the glass raw material tends to remain melted. Therefore, from the viewpoint of improving the meltability and low-temperature softening properties of the glass, the upper limit of the content of SiO 2 is preferably the above-mentioned range.

在本實施形態的光學玻璃中，Al2 O3 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%。此外，Al2 O3 的含量的下限較佳為0%。另外，Al2 O3 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Al 2 O 3 is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. %. Further, the lower limit of the content of Al 2 O 3 is preferably 0%. In addition, the content of Al 2 O 3 may be 0%.

Al2 O3 為具有改善玻璃的化學耐久性、耐候性的作用的玻璃成分，可以考慮作為網絡形成成分。但是，當Al2 O3 的含量增多時，容易產生折射率(nd)降低、玻璃的熱穩定性降低、玻璃化轉變溫度(Tg)上升、熔融性降低等問題。從避免這樣的問題的觀點出發，Al2 O3 的含量的上限較佳為上述範圍。Al 2 O 3 is a glass component having an effect of improving chemical durability and weather resistance of glass, and can be considered as a network-forming component. However, when the content of Al 2 O 3 increases, problems such as a decrease in the refractive index (nd), a decrease in the thermal stability of the glass, an increase in the glass transition temperature (Tg), and a decrease in meltability are likely to occur. From the viewpoint of avoiding such a problem, the upper limit of the content of Al 2 O 3 is preferably the above range.

在本實施形態的光學玻璃中，玻璃的網絡形成成分B2 O3 、SiO2 及Al2 O3 的合計含量[B2 O3 +SiO2 +Al2 O3 ]的上限較佳為34%，進而依次更佳為32%、30%、28%、26%、25%、24%。此外，合計含量[B2 O3 +SiO2 +Al2 O3 ]的下限較佳為10%，進而依次更佳為13%、15%、17%、18%、19%。In the optical glass of the present embodiment, the upper limit of the total content [B 2 O 3 +SiO 2 +Al 2 O 3 ] of the network-forming components B 2 O 3 , SiO 2 and Al 2 O 3 of the glass is preferably 34% , and more preferably 32%, 30%, 28%, 26%, 25%, and 24% in this order. In addition, the lower limit of the total content [B 2 O 3 +SiO 2 +Al 2 O 3 ] is preferably 10%, and more preferably 13%, 15%, 17%, 18%, and 19% in this order.

藉由將合計含量[B2 O3 +SiO2 +Al2 O3 ]的上限設為上述範圍，從而容易將折射率維持在所需的範圍。此外，藉由將合計含量[B2 O3 +SiO2 +Al2 O3 ]的下限設為上述範圍，從而可改善玻璃的熱穩定性、容易進一步抑制玻璃的失透。By setting the upper limit of the total content [B 2 O 3 +SiO 2 +Al 2 O 3 ] to the above range, it becomes easy to maintain the refractive index in a desired range. Moreover, by setting the lower limit of the total content [B 2 O 3 +SiO 2 +Al 2 O 3 ] to the above range, the thermal stability of the glass can be improved, and the devitrification of the glass can be further easily suppressed.

此外，在本實施形態的光學玻璃中，B2 O3 的含量相對於B2 O3 、SiO2 及Al2 O3 的合計含量的質量比[B2 O3 / (B2 O3 +SiO2 +Al2 O3 )]的下限較佳為0.50，進而依次更佳為0.60、0.70、0.80、0.85。也能夠將質量比[B2 O3 /(B2 O3 +SiO2 + Al2 O3 )]設為1。In addition, in the optical glass of the present embodiment, the mass ratio of the content of B 2 O 3 to the total content of B 2 O 3 , SiO 2 and Al 2 O 3 [B 2 O 3 /(B 2 O 3 +SiO The lower limit of 2 +Al 2 O 3 )] is preferably 0.50, and more preferably 0.60, 0.70, 0.80, and 0.85 in this order. The mass ratio [B 2 O 3 /(B 2 O 3 +SiO 2 +Al 2 O 3 )] can also be set to 1.

當質量比[B2 O3 /(B2 O3 +SiO2 +Al2 O3 )]小時，有玻璃的熔融性下降並且玻璃化轉變溫度Tg上升的傾向。因此，從維持良好的熔融性、玻璃的低溫軟化性的觀點出發，質量比[B2 O3 /(B2 O3 +SiO2 +Al2 O3 )]的下限較佳為上述範圍。When the mass ratio [B 2 O 3 /(B 2 O 3 +SiO 2 +Al 2 O 3 )] is small, the meltability of the glass tends to decrease and the glass transition temperature Tg tends to increase. Therefore, the lower limit of the mass ratio [B 2 O 3 /(B 2 O 3 +SiO 2 +Al 2 O 3 )] is preferably the above range from the viewpoint of maintaining good meltability and low-temperature softening properties of the glass.

也能夠將質量比[B2 O3 /(B2 O3 +SiO2 +Al2 O3 )]設為1，但是藉由含有少量SiO2 ，從而容易使成型時的熔融玻璃的黏度成為適合於成型的黏度。The mass ratio [B 2 O 3 /(B 2 O 3 +SiO 2 +Al 2 O 3 )] can also be set to 1, but by containing a small amount of SiO 2 , the viscosity of the molten glass at the time of molding can be easily adjusted viscosity for molding.

在本實施形態的光學玻璃中，La2 O3 、Gd2 O3 、Y2 O3 及Yb2 O3 的合計含量[La2 O3 +Gd2 O3 +Y2 O3 +Yb2 O3 ]的上限較佳為65%，進而依次更佳為60%、57%、55%、53%、52%。此外，合計含量[La2 O3 +Gd2 O3 +Y2 O3 +Yb2 O3 ]的下限較佳為35%，進而依次更佳為38%、41%、44%、45%、46%。In the optical glass of the present embodiment, the total content of La 2 O 3 , Gd 2 O 3 , Y 2 O 3 and Yb 2 O 3 [La 2 O 3 +Gd 2 O 3 +Y 2 O 3 +Yb 2 O 3 ] The upper limit is preferably 65%, and more preferably 60%, 57%, 55%, 53%, and 52% in this order. Further, the lower limit of the total content [La 2 O 3 +Gd 2 O 3 +Y 2 O 3 +Yb 2 O 3 ] is preferably 35%, more preferably 38%, 41%, 44%, 45%, 46%.

從實現所需的折射率、阿貝數的觀點出發，合計含量[La2 O3 +Gd2 O3 +Y2 O3 +Yb2 O3 ]的下限較佳為上述範圍。從改善玻璃的熱穩定性、低溫軟化性的觀點出發，合計含量[La2 O3 +Gd2 O3 +Y2 O3 +Yb2 O3 ]的上限較佳為上述範圍。From the viewpoint of achieving the desired refractive index and Abbe number, the lower limit of the total content [La 2 O 3 +Gd 2 O 3 +Y 2 O 3 +Yb 2 O 3 ] is preferably the above range. From the viewpoint of improving the thermal stability and low-temperature softening properties of the glass, the upper limit of the total content [La 2 O 3 +Gd 2 O 3 +Y 2 O 3 +Yb 2 O 3 ] is preferably the above range.

在本實施形態的光學玻璃中，La2 O3 的含量的上限較佳為50%，進而依次更佳為45%、42%、40%、38%、37%。此外，La2 O3 的含量的下限較佳為10%，進而依次更佳為15%、17%、19%、20%、21%、22%。In the optical glass of the present embodiment, the upper limit of the content of La 2 O 3 is preferably 50%, and more preferably 45%, 42%, 40%, 38%, and 37% in this order. In addition, the lower limit of the content of La 2 O 3 is preferably 10%, and more preferably 15%, 17%, 19%, 20%, 21%, and 22% in this order.

La2 O3 除了上述的作用以外還具有改善玻璃的化學耐久性的作用。進而，在稀土類氧化物成分中，La2 O3 是即使含量較多也不易使熱穩定性降低的成分。因此，從改善玻璃的熱穩定性、化學耐久性的觀點出發，La2 O3 的含量的下限較佳為上述範圍。此外，從改善玻璃的熱穩定性的觀點出發，La2 O3 的含量的上限較佳為上述範圍。La 2 O 3 has the effect of improving the chemical durability of glass in addition to the above-mentioned functions. Furthermore, among the rare earth oxide components, La 2 O 3 is a component that does not easily reduce thermal stability even if the content thereof is large. Therefore, from the viewpoint of improving the thermal stability and chemical durability of the glass, the lower limit of the content of La 2 O 3 is preferably the above range. Moreover, from the viewpoint of improving the thermal stability of the glass, the upper limit of the content of La 2 O 3 is preferably the above range.

在本實施形態的光學玻璃中，Gd2 O3 的含量的上限較佳為50%，進而依次更佳為45%、40%、35%、31%、30%、29%。此外，Gd2 O3 的含量的下限較佳為1%，進而依次更佳為2%、3%、5%、7%、10%、11%、12%。In the optical glass of the present embodiment, the upper limit of the content of Gd 2 O 3 is preferably 50%, and more preferably 45%, 40%, 35%, 31%, 30%, and 29% in this order. In addition, the lower limit of the content of Gd 2 O 3 is preferably 1%, and more preferably 2%, 3%, 5%, 7%, 10%, 11%, and 12% in this order.

Gd2 O3 除了上述的作用以外還具有改善玻璃的化學耐久性的作用。進而，Gd2 O3 藉由在玻璃中與La2 O3 共存，從而還具有提高玻璃的熱穩定性的作用。因此，從改善玻璃的熱穩定性、化學耐久性的觀點出發，Gd2 O3 的含量的下限較佳為上述範圍。此外，從改善玻璃的熱穩定性的觀點出發，Gd2 O3 的含量的上限較佳為上述範圍。Gd 2 O 3 has the effect of improving the chemical durability of glass in addition to the above-mentioned functions. Furthermore, Gd 2 O 3 also has the effect of improving the thermal stability of the glass by coexisting with La 2 O 3 in the glass. Therefore, from the viewpoint of improving the thermal stability and chemical durability of the glass, the lower limit of the content of Gd 2 O 3 is preferably the above range. Further, from the viewpoint of improving the thermal stability of the glass, the upper limit of the content of Gd 2 O 3 is preferably the above range.

在本實施形態的光學玻璃中，Y2 O3 的含量的上限較佳為10%，進而依次更佳為8%、5%、4%、3%。此外，Y2 O3 的含量的下限較佳為0%。另外，Y2 O3 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Y 2 O 3 is preferably 10%, and more preferably 8%, 5%, 4%, and 3% in this order. Further, the lower limit of the content of Y 2 O 3 is preferably 0%. In addition, the content of Y 2 O 3 may be 0%.

Y2 O3 除了上述的作用以外還具有改善玻璃的化學耐久性的作用。進而，Y2 O3 藉由在玻璃中與La2 O3 共存，從而還具有提高玻璃的熱穩定性的作用。因此，從改善玻璃的熱穩定性的觀點出發，Y2 O3 的含量較佳為上述範圍。In addition to the above-mentioned functions, Y 2 O 3 has the effect of improving the chemical durability of the glass. Furthermore, Y 2 O 3 also has the effect of improving the thermal stability of the glass by coexisting with La 2 O 3 in the glass. Therefore, from the viewpoint of improving the thermal stability of the glass, the content of Y 2 O 3 is preferably within the above range.

在本實施形態的光學玻璃中，Yb2 O3 的含量的上限較佳為3%，進而依次更佳為2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Yb2 O3 的含量的下限較佳為0%。另外，Yb2 O3 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Yb 2 O 3 is preferably 3%, and more preferably 2.5%, 2%, 1.5%, 1%, 0.5%, 0.1%, and 0.05% in this order. Further, the lower limit of the content of Yb 2 O 3 is preferably 0%. In addition, the content of Yb 2 O 3 may be 0%.

Yb2 O3 與La2 O3 、Gd2 O3 及Y2 O3 同樣是具有在不使阿貝數大幅降低的情況下提高折射率的作用的玻璃成分。但是，與La2 O3 、Gd2 O3 、Y2 O3 相比Yb2 O3 的分子量大，因此會使玻璃的比重增大。當玻璃的比重增大時，光學元件的質量會增大。例如，如果將質量大的透鏡組裝到自動對焦式的攝像鏡頭，在自動對焦時驅動鏡頭所需的功率就會增大，電池的消耗加劇。因此，期望降低Yb2 O3 的含量來抑制玻璃的比重增大。Yb 2 O 3 is a glass component having an effect of increasing the refractive index without significantly lowering the Abbe number, similarly to La 2 O 3 , Gd 2 O 3 and Y 2 O 3 . However, since Yb 2 O 3 has a larger molecular weight than La 2 O 3 , Gd 2 O 3 and Y 2 O 3 , the specific gravity of the glass increases. As the specific gravity of the glass increases, the mass of the optical element increases. For example, if a lens with a large mass is incorporated into an auto-focus-type imaging lens, the power required to drive the lens during auto-focusing increases, and battery consumption increases. Therefore, it is desired to reduce the content of Yb 2 O 3 to suppress an increase in the specific gravity of the glass.

此外，Yb2 O3 在近紅外區域具有吸收。因此，Yb2 O3 的含量多的玻璃在近紅外區域的光吸收強，對於監視攝像機、夜視攝像機等在近紅外區域要求高透射率的用途不是較佳的。從改善這樣的問題的觀點出發，Yb2 O3 的含量較佳為上述範圍。In addition, Yb 2 O 3 has absorption in the near-infrared region. Therefore, glass with a high content of Yb 2 O 3 has strong light absorption in the near-infrared region, and is not preferable for applications requiring high transmittance in the near-infrared region, such as surveillance cameras and night vision cameras. From the viewpoint of improving such problems, the content of Yb 2 O 3 is preferably within the above range.

在本實施形態的光學玻璃中，LaF3 的含量的上限根據鹵化物的含量來決定，因此沒有特別限制，但是較佳為5%，進而依次更佳為3%、2%、1%、0.5%。此外，LaF3 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of LaF 3 is determined by the content of the halide, and therefore is not particularly limited, but is preferably 5%, and more preferably 3%, 2%, 1%, and 0.5% in this order. %. In addition, the content of LaF 3 may be 0%.

在本實施形態的光學玻璃中，GdF3 的含量的上限根據鹵化物的含量來決定，因此沒有特別限制，但是較佳為5%，進而依次更佳為3%、2%、1%、0.5%。此外，GdF3 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of GdF 3 is determined by the content of the halide, and therefore is not particularly limited, but is preferably 5%, more preferably 3%, 2%, 1%, and 0.5% in this order. %. In addition, the content of GdF 3 may be 0%.

在本實施形態的光學玻璃中，YF3 的含量的上限根據鹵化物的含量來決定，因此沒有特別限制，但是較佳為5%，進而依次更較佳為3%、2%、1%、0.5%。此外，YF3 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of YF 3 is determined by the content of the halide, and therefore is not particularly limited, but is preferably 5%, more preferably 3%, 2%, 1%, 0.5%. In addition, the content of YF 3 may be 0%.

在本實施形態的光學玻璃中，YbF3 的含量的上限根據鹵化物的含量來決定，因此沒有特別限制，但是較佳為3%，進而依次更佳為2%、1%、0.5%。此外，YbF3 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of YbF 3 is determined by the content of the halide, and therefore is not particularly limited, but is preferably 3%, more preferably 2%, 1%, and 0.5% in this order. In addition, the content of YbF 3 may be 0%.

在本實施形態的光學玻璃中，La2 O3 的含量相對於La2 O3 、Gd2 O3 、Y2 O3 及Yb2 O3 的合計含量[La2 O3 +Gd2 O3 + Y2 O3 +Yb2 O3 ]的質量比[La2 O3 /(La2 O3 +Gd2 O3 +Y2 O3 +Yb2 O3 )]的上限較佳為0.99，進而依次更佳為0.95、0.90、0.85、0.80、0.76、0.74、0.73。此外，質量比[La2 O3 /(La2 O3 +Gd2 O3 +Y2 O3 + Yb2 O3 )]的下限較佳為0.3，進而依次更佳為0.35、0.4、0.45、0.46。 In the optical glass of the present embodiment, the content of La 2 O 3 is [ La 2 O 3 + Gd 2 O 3 + The upper limit of the mass ratio of Y 2 O 3 +Yb 2 O 3 ] [La 2 O 3 /(La 2 O 3 +Gd 2 O 3 +Y 2 O 3 +Yb 2 O 3 )] is preferably 0.99, and further More preferably, it is 0.95, 0.90, 0.85, 0.80, 0.76, 0.74, 0.73. Further, the lower limit of the mass ratio [La 2 O 3 /(La 2 O 3 +Gd 2 O 3 +Y 2 O 3 + Yb 2 O 3 )] is preferably 0.3, more preferably 0.35, 0.4, 0.45, 0.46.

藉由使質量比[La2 O3 /(La2 O3 +Gd2 O3 +Y2 O3 + Yb2 O3 )]的上限為上述範圍，從而能夠將熱穩定性、熔融性維持為良好的狀態。此外，藉由使質量比[La2 O3 /(La2 O3 +Gd2 O3 +Y2 O3 + Yb2 O3 )]的下限為上述範圍，從而能夠將熱穩定性、熔融性維持為良好的狀態。By making the upper limit of the mass ratio [La 2 O 3 /(La 2 O 3 +Gd 2 O 3 +Y 2 O 3 + Yb 2 O 3 )] within the above range, thermal stability and meltability can be maintained at in good condition. Further, by setting the lower limit of the mass ratio [La 2 O 3 /(La 2 O 3 +Gd 2 O 3 +Y 2 O 3 + Yb 2 O 3 )] to the above range, thermal stability and meltability can be improved maintained in good condition.

在本實施形態的光學玻璃中，ZnO的含量的上限較佳為25%，進而依次更佳為22%、20%、18%、17%、16%。此外，ZnO的含量的下限較佳為5%，進而依次更佳為8%、9%、10%、11%。In the optical glass of the present embodiment, the upper limit of the content of ZnO is preferably 25%, and more preferably 22%, 20%, 18%, 17%, and 16% in this order. In addition, the lower limit of the content of ZnO is preferably 5%, and more preferably 8%, 9%, 10%, and 11% in this order.

ZnO是具有在維持折射率的同時使玻璃化轉變溫度(Tg)降低的作用和在將玻璃熔融時促進玻璃的原料的熔融的作用(即，改善熔融性的作用)的玻璃成分。此外，與鹼土類金屬等其它二價金屬成分相比，ZnO改善玻璃的熱穩定性、降低液相線溫度的作用強。但是，當ZnO的含量增多時，示出阿貝數(νd)減少、玻璃高色散化的傾向。因此，從降低玻璃化轉變溫度(Tg)、改善玻璃的熔融性、熱穩定性的觀點出發，ZnO的含量的下限較佳為上述範圍。此外，從使玻璃低色散化的觀點出發，ZnO的含量的上限較佳為上述範圍。ZnO is a glass component that has the effect of lowering the glass transition temperature (Tg) while maintaining the refractive index and the effect of promoting melting of the raw material of the glass when the glass is melted (that is, the effect of improving the meltability). In addition, compared with other divalent metal components such as alkaline earth metals, ZnO has a strong effect of improving the thermal stability of glass and lowering the liquidus temperature. However, when the content of ZnO increases, the Abbe number (νd) decreases and the glass tends to be highly dispersed. Therefore, from the viewpoint of lowering the glass transition temperature (Tg) and improving the meltability and thermal stability of the glass, the lower limit of the content of ZnO is preferably the above range. Moreover, it is preferable that the upper limit of content of ZnO is the said range from a viewpoint of making glass low-dispersion.

在本實施形態的光學玻璃中，Li2 O的含量的上限較佳為4.0%，進而依次更佳為3.0%、2.0%、1.6%、1.2%、0.8%、0.4%。此外，Li2 O的含量的下限較佳為0%。In the optical glass of the present embodiment, the upper limit of the content of Li 2 O is preferably 4.0%, and more preferably 3.0%, 2.0%, 1.6%, 1.2%, 0.8%, and 0.4% in this order. Further, the lower limit of the content of Li 2 O is preferably 0%.

Li2 O是降低玻璃化轉變溫度(Tg)的作用強、對於得到低溫軟化性有用的玻璃成分。此外，Li2 O還發揮改善玻璃的熔融性的作用。另一方面，當Li2 O的含量增多時，有折射率(nd)降低的傾向。因此，從在維持所需的光學特性的同時降低玻璃化轉變溫度(Tg)的觀點出發，Li2 O的含量較佳為上述範圍。Li 2 O is a glass component that has a strong effect of lowering the glass transition temperature (Tg) and is useful for obtaining low-temperature softening properties. In addition, Li 2 O also functions to improve the meltability of glass. On the other hand, when the content of Li 2 O increases, the refractive index (nd) tends to decrease. Therefore, from the viewpoint of lowering the glass transition temperature (Tg) while maintaining desired optical properties, the content of Li 2 O is preferably within the above range.

在本實施形態的光學玻璃中，ZrO2 的含量的上限較佳為15%，進而依次更佳為12%、10%、8%、7%、6%。此外，ZrO2 的含量的下限較佳為0.1%，進而依次更佳為0.5%、1.0%、1.5%、2.0%、2.5%、3.0%。In the optical glass of the present embodiment, the upper limit of the content of ZrO 2 is preferably 15%, and more preferably 12%, 10%, 8%, 7%, and 6% in this order. In addition, the lower limit of the content of ZrO 2 is preferably 0.1%, and more preferably 0.5%, 1.0%, 1.5%, 2.0%, 2.5%, and 3.0% in this order.

ZrO2 為具有提高折射率(nd)並且改善玻璃的熱穩定性的作用的玻璃成分。但是，當ZrO2 的含量過多時，示出玻璃的熱穩定性降低的傾向，玻璃化轉變溫度(Tg)上升，此外，玻璃原料容易產生熔融殘留。因此，從抑制玻璃化轉變溫度(Tg)的上升、良好地維持玻璃的熔融性和熱穩定性、實現所需的光學特性的觀點出發，ZrO2 的含量的上限較佳為上述範圍。另一方面，從在實現所需的光學特性的同時改善玻璃的熱穩定性的觀點出發，ZrO2 的含量的下限較佳為上述範圍。ZrO 2 is a glass component having the effect of increasing the refractive index (nd) and improving the thermal stability of the glass. However, when the content of ZrO 2 is too large, the thermal stability of the glass tends to decrease, the glass transition temperature (Tg) increases, and the glass raw material tends to remain melted. Therefore, the upper limit of the content of ZrO 2 is preferably the above-mentioned range from the viewpoint of suppressing the rise of the glass transition temperature (Tg), maintaining the meltability and thermal stability of the glass favorably, and realizing the desired optical properties. On the other hand, the lower limit of the content of ZrO 2 is preferably the above-mentioned range from the viewpoint of improving the thermal stability of the glass while achieving desired optical properties.

在本實施形態的光學玻璃中，Nb2 O5 的含量的上限較佳為15%，進而依次更佳為12%、10%、9%、8%、7%、6%。此外，Nb2 O5 的含量的下限較佳為0.1%，進而依次更佳為0.3%、0.5%、1.0%、1.2%、1.5%、2.0%。In the optical glass of the present embodiment, the upper limit of the content of Nb 2 O 5 is preferably 15%, and more preferably 12%, 10%, 9%, 8%, 7%, and 6% in this order. In addition, the lower limit of the content of Nb 2 O 5 is preferably 0.1%, and more preferably 0.3%, 0.5%, 1.0%, 1.2%, 1.5%, and 2.0% in this order.

Nb2 O5 具有提高折射率並且改善玻璃的熱穩定性的作用。此外，還具有改善玻璃的化學耐久性的作用。Nb2 O5 是替代具有高折射率低色散特性且改善玻璃的熱穩定性的作用大的Ta2 O5 的玻璃成分，是對於降低極其昂貴且具有使玻璃的熔融性降低的作用的Ta2 O5 的含量重要的玻璃成分。Nb 2 O 5 has the effect of increasing the refractive index and improving the thermal stability of the glass. In addition, it has the effect of improving the chemical durability of the glass. Nb 2 O 5 is a glass component that replaces Ta 2 O 5 which has high refractive index and low dispersion properties and has a great effect of improving the thermal stability of glass, and is Ta 2 which is extremely expensive and has the effect of reducing the meltability of glass. O 5 content is an important glass component.

當Nb2 O5 的含量過多時，示出玻璃的熱穩定性降低的傾向，並且示出阿貝數(νd)減小、玻璃高色散化的傾向。此外，有玻璃的著色變強的傾向。因此，從維持玻璃的熱穩定性的觀點出發，Nb2 O5 的含量的下限較佳為上述範圍。另一方面，從維持玻璃的熱穩定性、抑制玻璃的著色增大的觀點出發，Nb2 O5 的含量的上限較佳為上述範圍。When the content of Nb 2 O 5 is too large, the thermal stability of the glass tends to decrease, and the Abbe number (νd) tends to decrease and the glass tends to be highly dispersed. Moreover, there exists a tendency for the coloring of glass to become strong. Therefore, from the viewpoint of maintaining the thermal stability of the glass, the lower limit of the content of Nb 2 O 5 is preferably the above range. On the other hand, the upper limit of the content of Nb 2 O 5 is preferably the above range from the viewpoint of maintaining the thermal stability of the glass and suppressing the increase in coloration of the glass.

在本實施形態的光學玻璃中，Ta2 O5 的含量的上限較佳為3%，進而依次更佳為2.5%、2%、1.5%、1%、0.5%、0.3%、0.2%、0.1%、0.05%。此外，Ta2 O5 的含量的下限較佳為0%。另外，Ta2 O5 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Ta 2 O 5 is preferably 3%, more preferably 2.5%, 2%, 1.5%, 1%, 0.5%, 0.3%, 0.2%, 0.1% in this order. %, 0.05%. Further, the lower limit of the content of Ta 2 O 5 is preferably 0%. In addition, the content of Ta 2 O 5 may be 0%.

如前所述，Ta2 O5 為具有高折射率低色散特性且具有改善玻璃的熱穩定性的作用的玻璃成分。與其它的玻璃成分相比較，Ta2 O5 是極其昂貴的成分，當Ta2 O5 的含量增多時，玻璃的生產成本會增大。此外，與其它的玻璃成分相比Ta2 O5 的分子量大，因此會使玻璃的比重增大，結果使玻璃制光學元件的重量增大。進而，當使Ta2 O5 的含量增加時，玻璃的熔融性會降低，在將玻璃熔融時容易產生玻璃原料的熔融殘留。因此，Ta2 O5 的含量較佳為上述範圍。As described above, Ta 2 O 5 is a glass component that has high refractive index and low dispersion properties and has an effect of improving the thermal stability of glass. Compared with other glass components, Ta 2 O 5 is an extremely expensive component, and when the content of Ta 2 O 5 increases, the production cost of glass increases. In addition, since Ta 2 O 5 has a larger molecular weight than other glass components, the specific gravity of the glass is increased, and as a result, the weight of the glass-made optical element is increased. Furthermore, when the content of Ta 2 O 5 is increased, the meltability of the glass decreases, and the melting residue of the glass raw material tends to occur when the glass is melted. Therefore, the content of Ta 2 O 5 is preferably within the above range.

在本實施形態的光學玻璃中，Nb2 O5 、TiO2 、WO3 及Bi2 O3 的合計含量[Nb2 O5 +TiO2 +WO3 +Bi2 O3 ]的上限較佳為15%，進而依次更佳為13%、12%、11%、10%、9%、8%、7%。此外，合計含量[Nb2 O5 +TiO2 +WO3 +Bi2 O3 ]的下限較佳為0.1%，進而依次更佳為0.3%、0.5%、1%、1.2%、1.5%、2%、3%、4%、5%。In the optical glass of the present embodiment, the upper limit of the total content of Nb 2 O 5 , TiO 2 , WO 3 and Bi 2 O 3 [Nb 2 O 5 +TiO 2 +WO 3 +Bi 2 O 3 ] is preferably 15 %, and more preferably 13%, 12%, 11%, 10%, 9%, 8%, and 7% in this order. In addition, the lower limit of the total content [Nb 2 O 5 +TiO 2 +WO 3 +Bi 2 O 3 ] is preferably 0.1%, more preferably 0.3%, 0.5%, 1%, 1.2%, 1.5%, 2 %, 3%, 4%, 5%.

TiO2 、WO3 及Bi2 O3 與Nb2 O5 一同是具有提高折射率的作用的玻璃成分，藉由適量含有，從而還具有改善玻璃的熱穩定性的作用。此外，當提高這些玻璃成分的含量時，阿貝數(νd)減小。因此，將這些玻璃成分稱為高折射率高色散化成分。從抑制阿貝數(νd)的減小、抑制玻璃的著色增大的觀點出發，合計含量[Nb2 O5 +TiO2 +WO3 +Bi2 O3 ]的上限較佳為上述範圍。此外，從在保持高折射率的同時改善玻璃的熱穩定性的觀點出發，合計含量[Nb2 O5 +TiO2 +WO3 +Bi2 O3 ]的下限較佳為上述範圍。TiO 2 , WO 3 and Bi 2 O 3 together with Nb 2 O 5 are glass components that have the effect of increasing the refractive index, and when they are contained in an appropriate amount, they also have the effect of improving the thermal stability of the glass. Furthermore, when the content of these glass components is increased, the Abbe number (νd) decreases. Therefore, these glass components are called high refractive index and high dispersion components. The upper limit of the total content [Nb 2 O 5 +TiO 2 +WO 3 +Bi 2 O 3 ] is preferably the above-mentioned range from the viewpoint of suppressing a decrease in Abbe's number (νd) and suppressing an increase in coloration of glass. In addition, the lower limit of the total content [Nb 2 O 5 +TiO 2 +WO 3 +Bi 2 O 3 ] is preferably the above range from the viewpoint of improving the thermal stability of the glass while maintaining a high refractive index.

在本實施形態的光學玻璃中，TiO2 、WO3 及Bi2 O3 的合計含量[TiO2 +WO3 +Bi2 O3 ]的上限較佳為15%，進而依次更佳為12%、10%、9%、8%、7%、6.5%。此外，合計含量[TiO2 +WO3 +Bi2 O3 ]的下限較佳為0%，進而依次更佳為0.1%、0.5%、1%、1.5%、2%、2.5%、3%。In the optical glass of the present embodiment, the upper limit of the total content of TiO 2 , WO 3 and Bi 2 O 3 [TiO 2 +WO 3 +Bi 2 O 3 ] is preferably 15%, more preferably 12%, 10%, 9%, 8%, 7%, 6.5%. Further, the lower limit of the total content [TiO 2 +WO 3 +Bi 2 O 3 ] is preferably 0%, and more preferably 0.1%, 0.5%, 1%, 1.5%, 2%, 2.5%, and 3% in this order.

在高折射率高色散化成分中，與Nb2 O5 相比，TiO2 、WO3 及Bi2 O3 容易使玻璃的著色增大。從抑制玻璃的著色增大的觀點出發，合計含量[TiO2 +WO3 +Bi2 O3 ]的上限較佳為上述範圍。Among the high-refractive-index and high-dispersion components, TiO 2 , WO 3 and Bi 2 O 3 tend to increase the coloration of glass compared to Nb 2 O 5 . The upper limit of the total content [TiO 2 +WO 3 +Bi 2 O 3 ] is preferably the above-mentioned range from the viewpoint of suppressing the increase in coloration of the glass.

在本實施形態的光學玻璃中，WO3 的含量的上限較佳為15%，進而依次更佳為13%、12%、11%、10%、9%、8%、7%。此外，WO3 的含量的下限較佳為0%，進而依次更佳為0.1%、0.5%、1%、1.5%、2%、2.5%、3%。In the optical glass of the present embodiment, the upper limit of the content of WO 3 is preferably 15%, and more preferably 13%, 12%, 11%, 10%, 9%, 8%, and 7% in this order. Further, the lower limit of the content of WO 3 is preferably 0%, and more preferably 0.1%, 0.5%, 1%, 1.5%, 2%, 2.5%, and 3% in this order.

在高折射率高色散化成分中，WO3 具有使玻璃化轉變溫度(Tg)降低的作用。但是，當WO3 的含量過多時，阿貝數(νd)減少，難以實現所需的光學特性。此外，玻璃的著色會增大。從抑制阿貝數(νd)的減小、防止玻璃的著色增大的觀點出發，WO3 的含量的上限較佳為上述範圍。另外，WO3 的含量也可以為0%。此外，為了得到WO3 的抑制玻璃化轉變溫度(Tg)上升的效果，WO3 的含量的下限較佳為上述範圍。Among the high refractive index and high dispersion components, WO 3 has the effect of lowering the glass transition temperature (Tg). However, when the content of WO 3 is too large, the Abbe number (νd) decreases, and it becomes difficult to achieve desired optical properties. In addition, the coloring of the glass increases. The upper limit of the content of WO 3 is preferably the above-mentioned range from the viewpoint of suppressing the decrease in Abbe's number (νd) and preventing the increase in coloration of the glass. In addition, the content of WO 3 may be 0%. Moreover, in order to obtain the effect of suppressing the glass transition temperature (Tg) rise of WO3, it is preferable that the lower limit of content of WO3 is the said range.

在本實施形態的光學玻璃中，TiO2 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%。此外，TiO2 的含量的下限較佳為0%。另外，TiO2 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of TiO 2 is preferably 5%, and more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. Further, the lower limit of the content of TiO 2 is preferably 0%. In addition, the content of TiO 2 may be 0%.

在高折射率高色散化成分中，TiO2 為比較容易使玻璃的著色增大的玻璃成分。此外，TiO2 在精密壓製成型時會與壓製成型模的成型面之間進行反應，其結果是，壓製成型後的玻璃的表面的透明性降低(白濁)，此外，容易使玻璃表面產生微小的氣泡。因此，從製作著色少、表面品質好的光學元件的觀點出發，TiO2 的含量較佳為上述範圍。Among the high-refractive-index and high-dispersion components, TiO 2 is a glass component that relatively easily increases the coloration of glass. In addition, TiO 2 reacts with the molding surface of the press molding die during precision press molding, and as a result, the transparency of the surface of the glass after press molding is reduced (white turbidity), and it is easy to generate microscopic particles on the glass surface. bubble. Therefore, the content of TiO 2 is preferably within the above-mentioned range from the viewpoint of producing an optical element with little coloration and good surface quality.

在本實施形態的光學玻璃中，Bi2 O3 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%。此外，Bi2 O3 的含量的下限較佳為0%。另外，Bi2 O3 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Bi 2 O 3 is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. %. Moreover, the lower limit of the content of Bi 2 O 3 is preferably 0%. In addition, the content of Bi 2 O 3 may be 0%.

在高折射率高色散化成分中，Bi2 O3 的分子量大，是使玻璃的比重增大並且使玻璃的著色增大的玻璃成分，因此較佳降低Bi2 O3 的含量。因此，Bi2 O3 的含量較佳為上述範圍。Among the high-refractive-index and high-dispersion components, Bi 2 O 3 has a large molecular weight and is a glass component that increases the specific gravity of the glass and increases the coloration of the glass, so it is preferable to reduce the content of Bi 2 O 3 . Therefore, the content of Bi 2 O 3 is preferably within the above range.

在本實施形態的光學玻璃中，Na2 O的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%。此外，Na2 O的含量的下限較佳為0%。另外，Na2 O的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Na 2 O is preferably 5%, and more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. . Further, the lower limit of the content of Na 2 O is preferably 0%. In addition, the content of Na 2 O may be 0%.

在本實施形態的光學玻璃中，K2 O的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%。此外，K2 O的含量的下限較佳為0%。另外，K2 O的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of K 2 O is preferably 5%, and more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. . Further, the lower limit of the content of K 2 O is preferably 0%. In addition, the content of K 2 O may be 0%.

Na2 O和K2 O均具有改善玻璃的熔融性的作用，但是當它們的含量增多時，折射率(nd)、玻璃的熱穩定性、化學耐久性、耐候性會下降。因此，Na2 O和K2 O的各含量分別較佳設為上述範圍。Both Na 2 O and K 2 O have the effect of improving the meltability of glass, but when their content increases, the refractive index (nd), thermal stability, chemical durability, and weather resistance of the glass decrease. Therefore, the respective contents of Na 2 O and K 2 O are preferably set to the above ranges.

在本實施形態的光學玻璃中，Li2 O、Na2 O及K2 O的合計含量[Li2 O+Na2 O+K2 O]的上限較佳為6%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%。此外，合計含量[Li2 O+Na2 O+K2 O]的下限較佳為0%。In the optical glass of the present embodiment, the upper limit of the total content of Li 2 O, Na 2 O and K 2 O [Li 2 O+Na 2 O+K 2 O] is preferably 6%, more preferably 4 in that order %, 3%, 2.5%, 2%, 1.5%, 1%. Further, the lower limit of the total content [Li 2 O+Na 2 O+K 2 O] is preferably 0%.

Li2 O是降低玻璃化轉變溫度(Tg)的作用強、對於得到低溫軟化性有用的玻璃成分。此外，Li2 O還發揮改善玻璃的熔融性的作用。另一方面，當Li2 O的含量增多時，有折射率(nd)降低的傾向。此外，Na2 O和K2 O均具有改善玻璃的熔融性的作用，但是當它們的含量增多時，折射率(nd)、玻璃的熱穩定性、化學耐久性、耐候性會降低。因此，Li2 O、Na2 O及K2 O的合計含量[Li2 O+Na2 O+K2 O]較佳為上述範圍。Li 2 O is a glass component that has a strong effect of lowering the glass transition temperature (Tg) and is useful for obtaining low-temperature softening properties. In addition, Li 2 O also functions to improve the meltability of glass. On the other hand, when the content of Li 2 O increases, the refractive index (nd) tends to decrease. In addition, both Na 2 O and K 2 O have the effect of improving the meltability of glass, but when their content increases, the refractive index (nd), thermal stability, chemical durability, and weather resistance of the glass decrease. Therefore, the total content of Li 2 O, Na 2 O and K 2 O [Li 2 O+Na 2 O+K 2 O] is preferably within the above range.

在本實施形態的光學玻璃中，Rb2 O的含量的上限較佳為3%，進而依次更佳為2.5%、2%、1.5%、1%、0.5%、0.1%。此外，Rb2 O的含量的下限較佳為0%。另外，Rb2 O的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Rb 2 O is preferably 3%, and more preferably 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. Further, the lower limit of the content of Rb 2 O is preferably 0%. In addition, the content of Rb 2 O may be 0%.

在本實施形態的光學玻璃中，Cs2 O的含量的上限較佳為3%，進而依次更佳為2.5%、2%、1.5%、1%、0.5%、0.1%。此外，Cs2 O的含量的下限較佳為0%。另外，Cs2 O的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Cs 2 O is preferably 3%, and more preferably 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. Further, the lower limit of the content of Cs 2 O is preferably 0%. In addition, the content of Cs 2 O may be 0%.

Rb2 O和Cs2 O均具有改善玻璃的熔融性的作用，但是當它們的含量增多時，折射率(nd)、玻璃的熱穩定性、化學耐久性、耐候性會下降。因此，Rb2 O和Cs2 O的各含量分別較佳為上述範圍。Both Rb 2 O and Cs 2 O have the effect of improving the meltability of glass, but when their content increases, the refractive index (nd), thermal stability, chemical durability, and weather resistance of the glass decrease. Therefore, the respective contents of Rb 2 O and Cs 2 O are preferably within the above ranges.

在本實施形態的光學玻璃中，MgO的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%。此外，MgO的含量的下限較佳為0%。另外，MgO的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of MgO is preferably 5%, and more preferably 4%, 3%, 2.5%, 2%, 1.5%, and 1% in this order. Further, the lower limit of the content of MgO is preferably 0%. In addition, the content of MgO may be 0%.

在本實施形態的光學玻璃中，CaO的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%。此外，CaO的含量的下限較佳為0%。另外，CaO的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of CaO is preferably 5%, and more preferably 4%, 3%, 2.5%, 2%, 1.5%, and 1% in this order. Further, the lower limit of the content of CaO is preferably 0%. In addition, the content of CaO may be 0%.

在本實施形態的光學玻璃中，SrO的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%。此外，SrO的含量的下限較佳為0%。另外，SrO的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of SrO is preferably 5%, and more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. Further, the lower limit of the content of SrO is preferably 0%. In addition, the content of SrO may be 0%.

在本實施形態的光學玻璃中，BaO的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%。此外，BaO的含量的下限較佳為0%。另外，BaO的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of BaO is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. Further, the lower limit of the content of BaO is preferably 0%. In addition, the content of BaO may be 0%.

MgO、CaO、SrO、BaO均為具有改善玻璃的熔融性的作用的玻璃成分。但是，當這些玻璃成分的含量增多時，玻璃的熱穩定性會降低，玻璃容易失透。因此，這些玻璃成分的各含量分別較佳為上述範圍。MgO, CaO, SrO, and BaO are all glass components that have the effect of improving the meltability of glass. However, when the content of these glass components increases, the thermal stability of the glass decreases, and the glass tends to devitrify. Therefore, it is preferable that each content of these glass components is the said range, respectively.

在本實施形態的光學玻璃中，MgO、CaO、SrO及BaO的合計含量[MgO+CaO+SrO+BaO]的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%。此外，合計含量[MgO+CaO+SrO+BaO]的下限較佳為0%。另外，合計含量[MgO+CaO+SrO+BaO]也可以為0%。In the optical glass of the present embodiment, the upper limit of the total content of MgO, CaO, SrO and BaO [MgO+CaO+SrO+BaO] is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%. Further, the lower limit of the total content [MgO+CaO+SrO+BaO] is preferably 0%. In addition, the total content [MgO+CaO+SrO+BaO] may be 0%.

從維持玻璃的熱穩定性的觀點出發，合計含量[MgO+CaO+SrO+BaO]較佳為上述範圍。From the viewpoint of maintaining the thermal stability of the glass, the total content [MgO+CaO+SrO+BaO] is preferably within the above range.

在本實施形態的光學玻璃中，B2 O3 、SiO2 、Al2 O3 、La2 O3 、Gd2 O3 、Y2 O3 、ZnO、Li2 O、ZrO2 及Nb2 O5 的合計含量[B2 O3 +SiO2 +Al2 O3 +La2 O3 +Gd2 O3 +Y2 O3 +ZnO+Li2 O+ZrO2 +Nb2 O5 ]的上限較佳為100%。此外，合計含量[B2 O3 +SiO2 +Al2 O3 + La2 O3 +Gd2 O3 +Y2 O3 +ZnO+Li2 O+ZrO2 +Nb2 O5 ]的下限較佳為79%，進而依次更佳為80%、82%、84%、86%、88%。In the optical glass of the present embodiment, B 2 O 3 , SiO 2 , Al 2 O 3 , La 2 O 3 , Gd 2 O 3 , Y 2 O 3 , ZnO, Li 2 O , ZrO 2 and Nb 2 O 5 The upper limit of the total content [B 2 O 3 +SiO 2 +Al 2 O 3 +La 2 O 3 +Gd 2 O 3 +Y 2 O 3 +ZnO+Li 2 O+ZrO 2 +Nb 2 O 5 ] is preferable is 100%. In addition, the lower limit of the total content [B 2 O 3 +SiO 2 +Al 2 O 3 + La 2 O 3 +Gd 2 O 3 +Y 2 O 3 +ZnO+Li 2 O+ZrO 2 +Nb 2 O 5 ] is relatively low The best is 79%, and then the better is 80%, 82%, 84%, 86%, 88%.

在本實施形態中，B2 O3 、SiO2 及Al2 O3 為玻璃的網絡形成成分，La2 O3 、Gd2 O3 及Y2 O3 為在不使阿貝數大幅減小的情況下提高折射率的玻璃成分，ZnO和Li2 O為具有在不使折射率大幅降低的情況下使玻璃化轉變溫度(Tg)降低的作用的玻璃成分，此外，ZrO2 和Nb2 O5 為具有提高玻璃的折射率並且改善玻璃的熱穩定性的作用的玻璃成分。因此，合計含量[B2 O3 +SiO2 +Al2 O3 +La2 O3 +Gd2 O3 +Y2 O3 +ZnO+Li2 O+ZrO2 +Nb2 O5 ]較佳為上述範圍。In this embodiment, B 2 O 3 , SiO 2 and Al 2 O 3 are network-forming components of glass, and La 2 O 3 , Gd 2 O 3 and Y 2 O 3 are those that do not significantly reduce the Abbe number. In the case of glass components that increase the refractive index, ZnO and Li 2 O are glass components that have the effect of lowering the glass transition temperature (Tg) without significantly lowering the refractive index, and ZrO 2 and Nb 2 O 5 It is a glass component having the effect of increasing the refractive index of the glass and improving the thermal stability of the glass. Therefore, the total content [B 2 O 3 +SiO 2 +Al 2 O 3 +La 2 O 3 +Gd 2 O 3 +Y 2 O 3 +ZnO+Li 2 O+ZrO 2 +Nb 2 O 5 ] is preferably the above range.

在本實施形態的光學玻璃中，三氧化二鎵(Ga2 O3 )的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%。此外，Ga2 O3 的含量的下限較佳為0%。另外，Ga2 O3 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of gallium trioxide (Ga 2 O 3 ) is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1 %, 0.5%, 0.1%. Further, the lower limit of the content of Ga 2 O 3 is preferably 0%. In addition, the content of Ga 2 O 3 may be 0%.

在本實施形態的光學玻璃中，三氧化二銦(In2 O3 )的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%。此外，In2 O3 的含量的下限較佳為0%。另外，In2 O3 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of indium trioxide (In 2 O 3 ) is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1 %, 0.5%, 0.1%. Further, the lower limit of the content of In 2 O 3 is preferably 0%. In addition, the content of In 2 O 3 may be 0%.

在本實施形態的光學玻璃中，三氧化二鈧(Sc2 O3 )的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%。此外，Sc2 O3 的含量的下限較佳為0%。另外，Sc2 O3 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of scandium trioxide (Sc 2 O 3 ) is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1 %, 0.5%, 0.1%. Further, the lower limit of the content of Sc 2 O 3 is preferably 0%. In addition, the content of Sc 2 O 3 may be 0%.

在本實施形態的光學玻璃中，二氧化鉿(HfO2 )的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%。此外，HfO2 的含量的下限較佳為0%。另外，HfO2 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of hafnium dioxide (HfO 2 ) is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5% in this order. %, 0.1%. Further, the lower limit of the content of HfO 2 is preferably 0%. In addition, the content of HfO 2 may be 0%.

Ga2 O3 、In2 O3 、Sc2 O3 、HfO2 均具有提高折射率(nd)的作用。但是，這些玻璃成分昂貴，此外，也不是對於達到發明的目的所必需的玻璃成分。因此，較佳Ga2 O3 、In2 O3 、Sc2 O3 、HfO2 的各含量為上述範圍。Ga 2 O 3 , In 2 O 3 , Sc 2 O 3 , and HfO 2 all have the effect of increasing the refractive index (nd). However, these glass components are expensive and are not necessary glass components to achieve the object of the invention. Therefore, the content of each of Ga 2 O 3 , In 2 O 3 , Sc 2 O 3 , and HfO 2 is preferably within the above range.

在本實施形態的光學玻璃中，Lu2 O3 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%。此外，Lu2 O3 的含量的下限較佳為0%。另外，Lu2 O3 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Lu 2 O 3 is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, 0.1% in this order. %. Further, the lower limit of the content of Lu 2 O 3 is preferably 0%. In addition, the content of Lu 2 O 3 may be 0%.

三氧化二鎦(Lu2 O3 )具有提高折射率(nd)的作用，但是與Yb2 O3 同樣分子量大，因此也是使玻璃的比重增加的玻璃成分。因此，較佳降低Lu2 O3 的含量，Lu2 O3 的含量較佳為上述範圍。Dilutetium trioxide (Lu 2 O 3 ) has the effect of increasing the refractive index (nd), but has a large molecular weight like Yb 2 O 3 , so it is also a glass component that increases the specific gravity of glass. Therefore, the content of Lu 2 O 3 is preferably reduced, and the content of Lu 2 O 3 is preferably within the above range.

在本實施形態的光學玻璃中，二氧化鍺(GeO2 )的含量的上限較佳為3%，進而依次更佳為2%、1%、0.5%、0.1%。此外，GeO2 的含量的下限較佳為0%。另外，GeO2 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of germanium dioxide (GeO 2 ) is preferably 3%, and more preferably 2%, 1%, 0.5%, and 0.1% in this order. Further, the lower limit of the content of GeO 2 is preferably 0%. In addition, the content of GeO 2 may be 0%.

GeO2 具有提高折射率(nd)的作用，但是在通常使用的玻璃成分中是尤其昂貴的成分。因此，從降低玻璃的製造成本的觀點出發，GeO2 的含量較佳為上述範圍。GeO 2 has the effect of increasing the refractive index (nd), but is an especially expensive component among commonly used glass components. Therefore, the content of GeO 2 is preferably within the above-mentioned range from the viewpoint of reducing the production cost of glass.

此外，在本實施形態的光學玻璃中，五氧化二磷(P2 O5 )的含量的上限較佳為5%，進而依次更佳為4%、3%、2%、1%、0.5%、0.1%。此外，P2 O5 的含量的下限較佳為0%。另外，P2 O5 的含量也可以為0%。In addition, in the optical glass of the present embodiment, the upper limit of the content of phosphorus pentoxide (P 2 O 5 ) is preferably 5%, and more preferably 4%, 3%, 2%, 1%, and 0.5% in this order. , 0.1%. Further, the lower limit of the content of P 2 O 5 is preferably 0%. In addition, the content of P 2 O 5 may be 0%.

P2 O5 是使折射率(nd)降低的玻璃成分，還是使玻璃的熱穩定性降低的成分。從製作具有所需的光學特性、熱穩定性優秀的玻璃的觀點出發，P2 O5 的含量較佳為上述範圍。P 2 O 5 is a glass component that lowers the refractive index (nd) or a component that lowers the thermal stability of glass. The content of P 2 O 5 is preferably within the above range from the viewpoint of producing glass having desired optical properties and excellent thermal stability.

本實施形態的光學玻璃較佳主要由上述的玻璃成分構成，即，較佳由B2 O3 、SiO2 、Al2 O3 、La2 O3 、Gd2 O3 、Y2 O3 、Yb2 O3 、LaF3 、GdF3 、YF3 、YbF3 、ZnO、Li2 O、ZrO2 、Nb2 O5 、Ta2 O5 、WO3 、TiO2 、Bi2 O3 、Na2 O、K2 O、Rb2 O、Cs2 O、MgO、CaO、SrO、BaO、Ga2 O3 、In2 O3 、Sc2 O3 、HfO2 、Lu2 O3 、Yb2 O3 、GeO2 及P2 O5 構成，上述的玻璃成分的合計含量較佳大於95%，更佳大於98%，進一步較佳大於99%，再進一步較佳大於99.5%。The optical glass of the present embodiment is preferably mainly composed of the above-mentioned glass components, that is, preferably B 2 O 3 , SiO 2 , Al 2 O 3 , La 2 O 3 , Gd 2 O 3 , Y 2 O 3 , and Yb 2O3 , LaF3 , GdF3 , YF3 , YbF3 , ZnO , Li2O , ZrO2 , Nb2O5 , Ta2O5 , WO3 , TiO2 , Bi2O3 , Na2O , K 2 O, Rb 2 O, Cs 2 O, MgO, CaO, SrO, BaO, Ga 2 O 3 , In 2 O 3 , Sc 2 O 3 , HfO 2 , Lu 2 O 3 , Yb 2 O 3 , GeO 2 and P 2 O 5 , the total content of the above-mentioned glass components is preferably greater than 95%, more preferably greater than 98%, further preferably greater than 99%, and still more preferably greater than 99.5%.

在本實施形態的光學玻璃中，TeO2 的含量的上限較佳為3%，進而依次更佳為2%、1%、0.5%、0.1%。此外，TeO2 的含量的下限較佳為0%。另外，TeO2 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of TeO 2 is preferably 3%, and more preferably 2%, 1%, 0.5%, and 0.1% in this order. Further, the lower limit of the content of TeO 2 is preferably 0%. In addition, the content of TeO 2 may be 0%.

TeO2 為提高折射率nd的成分，但是具有毒性，因此較佳降低TeO2 的含量。因此，TeO2 的含量較佳為上述範圍。TeO 2 is a component that increases the refractive index nd, but has toxicity, so it is preferable to reduce the content of TeO 2 . Therefore, the content of TeO 2 is preferably within the above range.

在本實施形態的光學玻璃中，在作為玻璃成分含有鹵化物的情況下，例如像LaF3 、GdF3 、YF3 、YbF3 那樣作為陽離子與鹵離子(陰離子)的化合物而含有。In the optical glass of the present embodiment, when a halide is contained as a glass component, for example, LaF 3 , GdF 3 , YF 3 , and YbF 3 are contained as a compound of a cation and a halide ion (anion).

導入到熔融玻璃的鹵化物的鹵離子的一部分被置換為同樣是陰離子且大量溶解在熔融玻璃中的氧離子。置換為氧離子的F- 、Cl- 、Br- 、I- 等鹵離子均成為氣體而從熔融玻璃揮發。由於鹵素的揮發，產生玻璃的特性改變、玻璃的均質性下降、熔融設備的消耗變得顯著等問題。因此，即使在含有鹵化物的情況下，也較佳減少其含量。Part of the halide ions of the halide introduced into the molten glass is replaced with oxygen ions which are also anions and dissolve in a large amount in the molten glass. Halogen ions such as F - , Cl - , Br - , and I - substituted with oxygen ions become gas and volatilize from the molten glass. Due to the volatilization of halogen, problems such as a change in the characteristics of the glass, a decrease in the homogeneity of the glass, and a significant consumption of the melting equipment occur. Therefore, even when a halide is contained, it is preferable to reduce its content.

由於上述理由，即使在作為玻璃成分含有鹵化物的情況下，也較佳將鹵化物的含量限制為少量，使得全部玻璃成分中的氧化物的比例(質量比)不會為95質量%以下。For the above reasons, even when a halide is contained as a glass component, it is preferable to limit the content of the halide to a small amount so that the ratio (mass ratio) of oxides in the entire glass component does not become 95% by mass or less.

即，在本實施形態的光學玻璃中，全部玻璃成分中的氧化物的含量較佳大於95質量%。進而，全部玻璃成分中的氧化物的含量的下限依次更較佳為97質量%、99質量%、99.5質量%、99.9質量%、99.95質量%、99.99質量%，全部玻璃成分中的氧化物的含量也可以為100質量%。全部玻璃成分中的氧化物的含量為100質量%的玻璃實質上不包含鹵化物。That is, in the optical glass of this embodiment, it is preferable that content of the oxide in all glass components exceeds 95 mass %. Furthermore, the lower limit of the content of oxides in all glass components is more preferably 97% by mass, 99% by mass, 99.5% by mass, 99.9% by mass, 99.95% by mass, 99.99% by mass, and the lower limit of the content of oxides in all glass components The content may be 100% by mass. The glass whose content of oxides in all glass components is 100 mass % contains substantially no halide.

另外，本實施形態的光學玻璃較佳基本上由上述玻璃成分構成，但是在不妨礙本發明的作用效果的範圍內，也能夠含有其它成分。此外，在本發明中，不排除含有不可避免的雜質。Further, the optical glass of the present embodiment is preferably basically composed of the above-mentioned glass components, but other components may be contained within a range that does not inhibit the functions and effects of the present invention. Further, in the present invention, the inclusion of inevitable impurities is not excluded.

＜其它的成分組成＞ 鉛(Pb)、砷(As)、鎘(Cd)、鉈(Tl)、鈹(Be)、硒(Se)均具有毒性。因此，較佳本實施形態的光學玻璃不含有這些元素作為玻璃成分。<Other ingredients> Lead (Pb), arsenic (As), cadmium (Cd), thallium (Tl), beryllium (Be), and selenium (Se) are all toxic. Therefore, it is preferable that the optical glass of this embodiment does not contain these elements as a glass component.

鈾(U)、釷(Th)、鐳(Ra)均為放射性元素。因此，較佳本實施形態的光學玻璃不含有這些元素作為玻璃成分。Uranium (U), thorium (Th), and radium (Ra) are all radioactive elements. Therefore, it is preferable that the optical glass of this embodiment does not contain these elements as a glass component.

釩(V)、鉻(Cr)、錳(Mn)、鐵(Fe)、鈷(Co)、鎳(Ni)、銅(Cu)、鐠(Pr)、釹(Nd)、鉕(Pm)、釤(Sm)、銪(Eu)、鋱(Tb)、鏑(Dy)、鈥(Ho)、鉺(Er)、銩(Tm)、鈰(Ce)會使玻璃的著色增大，可能成為螢光的產生源。因此，較佳本實施形態的光學玻璃不含有這些元素作為玻璃成分。Vanadium (V), Chromium (Cr), Manganese (Mn), Iron (Fe), Cobalt (Co), Nickel (Ni), Copper (Cu), Fe (Pr), Neodymium (Nd), Ni (Pm), Samarium (Sm), europium (Eu), titanium (Tb), dysprosium (Dy), ∥ (Ho), erbium (Er), tantalum (Tm), and cerium (Ce) will increase the coloring of the glass and may become fluorescent. source of light. Therefore, it is preferable that the optical glass of this embodiment does not contain these elements as a glass component.

Sb(Sb2 O3 )、Sn(SnO2 )、Ce(CeO2 )為作為澄清劑發揮功能的能夠任選添加的元素。其中，Sb(Sb2 O3 )為澄清效果大的澄清劑。但是，Sb(Sb2 O3 )的氧化性強，如果使Sb(Sb2 O3 )的添加量增多，在精密壓製成型時玻璃所包含的Sb(Sb2 O3 )就會氧化壓製成型模的成型面。因此，在重複進行精密壓製成型的過程中成型面會顯著劣化，變得不能進行精密壓製成型。此外，成型的光學元件的表面品質會降低。與Sb(Sb2 O3 )相比，Sn(SnO2 )、Ce(CeO2 )的澄清效果小。當大量添加Ce(CeO2 )時，玻璃的著色會變強。因此，在添加澄清劑的情況下，較佳在添加Sb(Sb2 O3 )的同時注意其添加量。Sb(Sb 2 O 3 ), Sn(SnO 2 ), and Ce(CeO 2 ) are optional elements that function as a clarifying agent. Among them, Sb (Sb 2 O 3 ) is a clarifying agent with a large clarifying effect. However, Sb (Sb 2 O 3 ) has strong oxidizing properties, and if the amount of Sb (Sb 2 O 3 ) added is increased, Sb (Sb 2 O 3 ) contained in the glass during precision press molding will oxidize the press molding die the molding surface. Therefore, in the process of repeating the precision press molding, the molding surface deteriorates remarkably, and it becomes impossible to perform the precision press molding. In addition, the surface quality of the molded optical element can be degraded. Sn(SnO 2 ) and Ce(CeO 2 ) have a smaller clarifying effect than Sb(Sb 2 O 3 ). When Ce(CeO 2 ) is added in a large amount, the coloring of glass becomes strong. Therefore, when adding a clarifying agent, it is preferable to pay attention to the addition amount while adding Sb ( Sb2O3 ) .

Sb2 O3 的含量以外加方式來表示。即，將Sb2 O3 、SnO2 及CeO2 以外的全部玻璃成分的合計含量設為100質量%時的Sb2 O3 的含量的範圍較佳為不足1質量%，更佳為不足0.5質量%，進一步較佳為不足0.1質量%。Sb2 O3 的含量也可以為0質量%。The content of Sb 2 O 3 is expressed in addition. That is, the range of the content of Sb 2 O 3 when the total content of all glass components other than Sb 2 O 3 , SnO 2 and CeO 2 is 100% by mass is preferably less than 1% by mass, more preferably less than 0.5% by mass %, more preferably less than 0.1 mass %. The content of Sb 2 O 3 may be 0 mass %.

SnO2 的含量也以外加方式來表示。即，將SnO2 、Sb2 O3 及CeO2 以外的全部玻璃成分的合計含量設為100質量%時的SnO2 的含量的範圍較佳為不足2質量%，更佳為不足1質量%，進一步較佳為不足0.5質量%，再進一步較佳為不足0.1質量%。SnO2 的含量也可以為0質量%。藉由將SnO2 的含量設為上述範圍，從而能夠改善玻璃的澄清性。The content of SnO 2 is also expressed externally. That is, the range of the SnO 2 content when the total content of all glass components other than SnO 2 , Sb 2 O 3 and CeO 2 is 100 mass % is preferably less than 2 mass %, more preferably less than 1 mass %, More preferably, it is less than 0.5 mass %, and still more preferably, it is less than 0.1 mass %. The content of SnO 2 may be 0 mass %. The clarity of glass can be improved by making content of SnO2 into the said range.

CeO2 的含量也為以外加方式來表示。即，將CeO2 、Sb2 O3 、SnO2 以外的全部玻璃成分的合計含量設為100質量%時的CeO2 的含量的範圍較佳為不足2質量%，更佳為不足1質量%，進一步較佳為不足0.5質量%，再進一步較佳為不足0.1質量%。CeO2 的含量也可以為0質量%。藉由將CeO2 的含量設為上述範圍，從而能夠改善玻璃的澄清性。The content of CeO 2 is also expressed in addition. That is, the range of the CeO 2 content when the total content of all glass components other than CeO 2 , Sb 2 O 3 , and SnO 2 is set to 100 mass % is preferably less than 2 mass %, more preferably less than 1 mass %, More preferably, it is less than 0.5 mass %, and still more preferably, it is less than 0.1 mass %. The content of CeO 2 may be 0 mass %. By making content of CeO2 into the said range, the clarity of glass can be improved.

本發明的實施形態的光學玻璃的折射率(nd)和阿貝數(νd)大、均質、著色少、玻璃化轉變溫度(Tg)低，因此適合於作為精密壓製成型用光學玻璃。The optical glass of the embodiment of the present invention has a large refractive index (nd) and Abbe number (νd), is homogeneous, has little coloration, and has a low glass transition temperature (Tg), and is therefore suitable as an optical glass for precision press molding.

本發明的實施形態的光學玻璃的玻璃組成例如能夠藉由ICP-AES(Inductively Coupled Plasma - Atomic Emission Spectrometry，電感耦合電漿原子發射光譜法)或者適宜地藉由離子色譜法、ICP-MS(Inductively Coupled Plasma - Mass Spectrometry，電感耦合電漿質譜法)等方法來進行定量。藉由ICP-AES求出的分析值有時包含例如分析值的±5%左右的測定誤差。此外，在本說明書和本發明中，玻璃的構成成分的含量為0%或不包含意味著實質上不包含該構成成分，指的是該構成成分的含量為雜質水平程度以下。The glass composition of the optical glass according to the embodiment of the present invention can be determined, for example, by ICP-AES (Inductively Coupled Plasma - Atomic Emission Spectrometry) or suitably by ion chromatography, ICP-MS (Inductively Coupled Plasma-Atomic Emission Spectrometry). Coupled Plasma - Mass Spectrometry, Inductively Coupled Plasma Mass Spectrometry) and other methods for quantification. The analytical value obtained by ICP-AES may include, for example, a measurement error of about ±5% of the analytical value. In addition, in this specification and the present invention, 0% or no content of a constituent component of the glass means that the constituent component is not substantially contained, and means that the content of the constituent component is equal to or less than the impurity level.

(玻璃特性) ＜玻璃化轉變溫度(Tg)＞ 本實施形態的光學玻璃的玻璃化轉變溫度(Tg)的上限較佳為630℃，進而依次更佳為625℃、620℃、615℃、610℃、605℃、600℃。此外，玻璃化轉變溫度Tg的下限較佳為570℃。(glass properties) <Glass transition temperature (Tg)> The upper limit of the glass transition temperature (Tg) of the optical glass of the present embodiment is preferably 630°C, more preferably 625°C, 620°C, 615°C, 610°C, 605°C, and 600°C in this order. Further, the lower limit of the glass transition temperature Tg is preferably 570°C.

藉由使玻璃化轉變溫度(Tg)的上限滿足上述範圍，從而在精密壓製成型時無需過度提高玻璃、壓製成型模的溫度即可進行高精度的壓製成型。其結果是，能夠降低壓製成型模的消耗，能夠延長壓製成型模的壽命。此外，藉由降低玻璃化轉變溫度(Tg)，從而能夠抑制精密壓製成型時的玻璃與壓製成型模的成型面的反應，能夠提高藉由壓製成型得到的光學元件表面的形狀精度，能夠提高表面的透明性。By making the upper limit of the glass transition temperature (Tg) satisfy the above-mentioned range, high-precision press-molding can be performed without excessively increasing the temperature of the glass or the press-molding mold during precision press-molding. As a result, the consumption of the press-molding mold can be reduced, and the life of the press-molding mold can be extended. In addition, by lowering the glass transition temperature (Tg), the reaction between the glass and the molding surface of the press molding die during precision press molding can be suppressed, the shape accuracy of the surface of the optical element obtained by press molding can be improved, and the surface can be improved. transparency.

＜玻璃的光線透射性＞ 在本實施形態中，光線透射性能夠藉由著色度(λ5)、著色度(λ80)來評價。<Light transmittance of glass> In the present embodiment, the light transmittance can be evaluated by the degree of coloration (λ5) and the degree of coloration (λ80).

使用具有2個互相平行的進行了光學拋光的平面的玻璃(厚度為10.0mm±0.1mm)，從上述2個平面中的一個平面使光線垂直地入射該平面。然後，算出從另一個平面射出的透射光的強度(Iout)與入射光的強度(Iin)的比(Iout/Iin)，即，算出外部透射率。使用分光光度計，一邊在例如280～700nm的範圍內掃描入射光的波長一邊測定外部透射率，由此得到光譜透射率曲線。A glass (10.0 mm±0.1 mm in thickness) having 2 optically polished planes parallel to each other was used, and light was incident perpendicularly to the plane from one of the 2 planes. Then, the ratio (Iout/Iin) of the intensity (Iout) of the transmitted light emitted from the other plane to the intensity (Iin) of the incident light, that is, the external transmittance is calculated. Using a spectrophotometer, the spectral transmittance curve is obtained by measuring the external transmittance while scanning the wavelength of the incident light in the range of, for example, 280 to 700 nm.

外部透射率隨著入射光的波長從玻璃的短波長側的吸收端向長波長側移動而增加，示出高的值。The external transmittance increases as the wavelength of incident light moves from the absorption end on the short wavelength side of the glass to the long wavelength side, showing a high value.

λ5為外部透射率成為5%的波長，λ80為外部透射率成為80%的波長。在280～700nm的波長區域中，在λ5的長波長側玻璃的外部透射率示出大於5%的值。此外，在上述波長區域中，在λ80的長波長側玻璃的外部透射率示出大於80%的值。λ5 is the wavelength at which the external transmittance becomes 5%, and λ80 is the wavelength at which the external transmittance becomes 80%. In the wavelength region of 280 to 700 nm, the external transmittance of the glass on the long wavelength side of λ5 showed a value greater than 5%. Further, in the above wavelength region, the external transmittance of the glass on the long wavelength side of λ80 shows a value greater than 80%.

藉由使用將λ80短波長化的光學玻璃，從而能夠提供可理想地再現色彩的光學元件。此外，藉由使用將λ5短波長化的光學玻璃，從而在使用紫外線固化型黏接劑對製作的光學元件進行黏接時，能夠充分地確保玻璃的紫外光的透射量(黏接劑的固化所需的量)，能夠提高黏接強度，進而能夠縮短紫外光的照射時間。By using the optical glass whose λ80 wavelength is shortened, it is possible to provide an optical element that can reproduce the color ideally. In addition, by using optical glass with a shorter wavelength of λ5, it is possible to sufficiently ensure the transmission amount of ultraviolet light of the glass (curing of the adhesive) when the optical element produced is bonded with an ultraviolet-curable adhesive. The required amount) can improve the bonding strength, and then can shorten the irradiation time of ultraviolet light.

根據這樣的理由，λ80的範圍較佳為450nm以下，更佳為445nm以下，進一步較佳為440nm以下。λ80的下限的目標為370nm。此外，λ5的範圍較佳為360nm以下，更佳為350nm以下。λ5的下限的目標為200nm。For such reasons, the range of λ80 is preferably 450 nm or less, more preferably 445 nm or less, and still more preferably 440 nm or less. The target of the lower limit of λ80 is 370 nm. Further, the range of λ5 is preferably 360 nm or less, more preferably 350 nm or less. The target of the lower limit of λ5 is 200 nm.

＜玻璃的比重＞ 本實施形態的光學玻璃為高折射率低色散玻璃且比重不大。通常，如果能夠降低玻璃的比重，就能夠減小透鏡的重量。其結果是，能夠降低搭載有透鏡的攝像機鏡頭的自動對焦驅動的功耗。另一方面，當過度減小比重時，會導致折射率(nd)的降低、熱穩定性的降低。因此，比重(d)的上限較佳為5.20，進而依次更佳為5.10、5.08、5.05。此外，從提高折射率、改善熱穩定性的觀點出發，比重(d)的下限較佳為4.2，進而依次更佳為4.3、4.4、4.5。<Specific gravity of glass> The optical glass of the present embodiment is a high-refractive-index, low-dispersion glass and has a low specific gravity. Generally, if the specific gravity of the glass can be reduced, the weight of the lens can be reduced. As a result, the power consumption of the autofocus driving of the lens-mounted camera lens can be reduced. On the other hand, when the specific gravity is excessively reduced, a decrease in the refractive index (nd) and a decrease in thermal stability are caused. Therefore, the upper limit of the specific gravity (d) is preferably 5.20, and more preferably 5.10, 5.08, and 5.05 in this order. In addition, from the viewpoint of increasing the refractive index and improving thermal stability, the lower limit of the specific gravity (d) is preferably 4.2, and more preferably 4.3, 4.4, and 4.5 in this order.

＜液相線溫度＞ 本實施形態的光學玻璃的液相線溫度的上限較佳為1200℃，進而依次更佳為1180℃、1170℃、1160℃、1150℃。此外，液相線溫度的下限較佳為970℃，進而依次更佳為980℃、1000℃、1030℃、1050℃。根據本實施形態的光學玻璃，可改善玻璃的熱穩定性，因此可得到在削減Ta的含量的同時玻璃化轉變溫度(Tg)低的高折射率低色散玻璃。<Liquidus temperature> The upper limit of the liquidus temperature of the optical glass of the present embodiment is preferably 1200°C, and more preferably 1180°C, 1170°C, 1160°C, and 1150°C in this order. Further, the lower limit of the liquidus temperature is preferably 970°C, and more preferably 980°C, 1000°C, 1030°C, and 1050°C in this order. According to the optical glass of the present embodiment, since the thermal stability of the glass can be improved, a high-refractive-index and low-dispersion glass having a low glass transition temperature (Tg) can be obtained while reducing the content of Ta.

(光學玻璃的製造) 本發明的實施形態的光學玻璃只要以成為上述規定的組成的方式調配玻璃原料並按照公知的玻璃製造方法對調配的玻璃原料進行製作即可。例如，調配複數種化合物並充分混合而制成批料原料，將批料原料放入到鉑坩堝中進行粗熔解(rough melt)。將藉由粗熔解得到的熔融物驟冷、粉碎而製作碎玻璃。進而將碎玻璃放入到鉑坩堝中進行加熱、再熔融(remelt)而製成熔融玻璃，進而在進行澄清、均質化後將熔融玻璃成型、緩冷而得到光學玻璃。熔融玻璃的成型、緩冷只要應用公知的方法進行即可。(Manufacture of optical glass) The optical glass which concerns on embodiment of this invention may mix|blend glass raw material so that it may become the said predetermined composition, and what is necessary is just to prepare the mixed glass raw material according to a well-known glass manufacturing method. For example, a plurality of compounds are prepared and sufficiently mixed to prepare a batch raw material, and the batch raw material is put into a platinum crucible for rough melting. The melt obtained by rough melting is rapidly cooled and pulverized to produce cullet. Furthermore, the cullet was put into a platinum crucible, heated and remelted to obtain a molten glass, and after further clarification and homogenization, the molten glass was shaped and slowly cooled to obtain an optical glass. The shaping|molding and slow cooling of a molten glass should just be performed by a well-known method.

另外，只要能夠在玻璃中導入所需含量的所需玻璃成分，調配批料原料時使用的化合物就沒有特別限定，作為這樣的化合物，可舉出氧化物、碳酸鹽、硝酸鹽、氫氧化物、氟化物等。In addition, the compound used in preparing the batch raw material is not particularly limited as long as the desired glass component can be introduced into the glass in the desired content. Examples of such compounds include oxides, carbonates, nitrates, and hydroxides. , fluoride, etc.

(光學元件等的製造) 使用本發明的實施形態的光學玻璃來製作光學元件時只要應用公知的方法即可。例如，將玻璃原料熔融而製成熔融玻璃，將該熔融玻璃流入到鑄模而成型為板狀，製作由本發明的光學玻璃構成的玻璃材料。然後，將該板狀的玻璃材料以規定體積分成幾部分，對玻璃表面進行拋光而製作精密壓製成型用玻璃材料(精密壓製成型用預製件)。(Manufacture of optical elements, etc.) When an optical element is produced using the optical glass of the embodiment of the present invention, a known method may be applied. For example, glass raw material is melted to obtain a molten glass, and the molten glass is poured into a mold and molded into a plate shape, thereby producing a glass material composed of the optical glass of the present invention. Then, the plate-shaped glass material is divided into several parts by a predetermined volume, and the glass surface is polished to produce a glass material for precision press molding (preform for precision press molding).

或者，將熔融玻璃滴下，將滴下的熔融玻璃滴成型而製作精密壓製成型用玻璃材料(精密壓製成型用預製件)。Alternatively, molten glass is dropped, and the dropped molten glass drop is molded to produce a glass material for precision press molding (preform for precision press molding).

接著，將這些精密壓製成型用預製件加熱、進行精密壓製成型而製作光學元件。在精密壓製成型後，也可以根據需要進行定心磨邊等加工。Next, these preforms for precision press molding are heated, and precision press molding is performed to produce optical elements. After precision press molding, it can also be processed such as centering and edging as required.

也可以根據使用目的在製作的光學元件的光學功能面鍍覆防反射膜、全反射膜等。Depending on the purpose of use, an antireflection film, a total reflection film, etc. may be plated on the optical function surface of the optical element to be produced.

作為光學元件，能夠例示非球面透鏡、微透鏡、透鏡陣列等各種透鏡、衍射光柵等。As the optical element, various lenses such as aspherical lenses, microlenses, and lens arrays, diffraction gratings, and the like can be exemplified.

第2實施形態 (以陽離子%表示的組成) 在本實施形態(第2實施形態)中，作為本發明的第2觀點，基於以陽離子%表示的各成分的含量對本發明的光學玻璃進行說明。因此，以下只要沒有特別說明，各含量就以陽離子%表示。Second Embodiment (Composition in % of cations) In this embodiment (2nd Embodiment), as a 2nd viewpoint of this invention, the optical glass of this invention is demonstrated based on the content of each component represented by cation %. Therefore, unless otherwise specified, each content is expressed in cation % below.

此外，在本說明書中，以陽離子%表示是指，對於以陽離子表示的各玻璃成分，用莫耳百分率來表示將全部的陽離子成分的合計含量設為100%時的各玻璃成分的含量。此外，合計含量是指複數種陽離子成分的含量(也包括含量為0%的情況)的合計量。此外，陽離子比是指以陽離子%表示的陽離子成分彼此的含量(也包括複數種陽離子成分的合計含量)的比例(比)。In addition, in this specification, the expression of cation % means that the content of each glass component when the total content of all cation components is set to 100% for each glass component represented by cations is represented by molar percentage. In addition, the total content means the total amount of the content of a plurality of cationic components (including the case where the content is 0%). In addition, the cation ratio means the ratio (ratio) of the content of cation components (including the total content of a plurality of cation components) expressed in cation %.

此外，陽離子成分的價數(例如B3+ 的價數為+3，Si4+ 的價數為+4，La3+ 的價數為+3，Nb5+ 的價數為+5，Ti4+ 的價數為+4，W6+ 的價數為+6)是根據本發明所屬技術領域慣用的值確定的。在該技術領域中，在以氧化物表示玻璃成分B、Si、La、Nb、Ti、W時表示為B2 O3 、SiO2 、La2 O3 、Nb2 O5 、TiO2 、WO3 也是根據在該技術領域中的慣用的標記法來確定的。因此，在分析玻璃組成時，可以不分析陽離子成分的價數。此外，陰離子成分的價數(例如O2- 的價數為-2)也與陽離子成分的價數同樣是根據慣用的值確定的，與像上述那樣將玻璃成分表示為例如氧化物B2 O3 、SiO2 、La2 O3 是同樣的。因此，在分析玻璃組成時，可以不分析陰離子成分的價數。In addition, the valence of the cationic component (for example, the valence of B3+ is +3 , the valence of Si4+ is +4, the valence of La3 + is +3, the valence of Nb5+ is +5, the valence of Ti The valence of 4+ is +4, and the valence of W 6+ is +6) is determined according to the values conventionally used in the technical field to which the present invention belongs. In this technical field, when the glass components B, Si, La, Nb, Ti, and W are expressed as oxides, they are expressed as B 2 O 3 , SiO 2 , La 2 O 3 , Nb 2 O 5 , TiO 2 , and WO 3 It is also determined according to the notation customary in this technical field. Therefore, when analyzing the glass composition, it is not necessary to analyze the valence of the cationic component. In addition, the valence of the anionic component (for example, the valence of O 2- is -2) is also determined from a conventional value like the valence of the cationic component, and it is not the same as when the glass component is represented by, for example, oxide B 2 O as described above. 3 , SiO 2 and La 2 O 3 are the same. Therefore, when analyzing the glass composition, it is not necessary to analyze the valence of the anion component.

另外，第2實施形態中的各玻璃成分的作用、效果與第1實施形態中的各玻璃成分的作用、效果相同，因此以下對於與第1實施形態的說明重複的事項，將以各成分的含量、合計含量、陽離子比的數值範圍(包括較佳的範圍)為中心進行說明，對上述重複事項進行適當省略。In addition, the functions and effects of the glass components in the second embodiment are the same as those of the glass components in the first embodiment. Therefore, the following items will be described as the same as those of the glass components in the first embodiment. The content, the total content, and the numerical range (including the preferred range) of the cation ratio will be mainly described, and the above-mentioned overlapping matters will be appropriately omitted.

本實施形態的光學玻璃為氧化物玻璃，在該光學玻璃中，RE2相對於NWF2的比[RE2/NWF2]為0.35以上；HR2相對於RE2的比[HR2/RE2]為0.33以下；Nb5+ 的含量相對於Nb5+ 和Ta5+ 的合計含量的陽離子比[Nb5+ /(Nb5+ +Ta5+ )]為3/4以上；RE2相對於D2的比[RE2/D2]為0.90以上；L2相對於NWF2和RE2的合計值的比[L2/(NWF2+RE2)]為0.78以上；阿貝數(νd)為39.0以上、45.0以下，對於該阿貝數(νd)，折射率(nd)滿足下述式(1)：nd≥2.235-0.01×νdThe optical glass of the present embodiment is an oxide glass, in which the ratio of RE2 to NWF2 [RE2/NWF2] is 0.35 or more, the ratio of HR2 to RE2 [HR2/RE2] is 0.33 or less, and Nb 5+ The cation ratio [Nb 5+ /(Nb 5+ +Ta 5+ )] of the content to the total content of Nb 5+ and Ta 5+ is 3/4 or more; the ratio of RE2 to D2 [RE2/D2] is 0.90 or more; the ratio of L2 to the total value of NWF2 and RE2 [L2/(NWF2+RE2)] is 0.78 or more; Abbe number (νd) is 39.0 or more and 45.0 or less, for this Abbe number (νd), refraction The rate (nd) satisfies the following formula (1): nd≥2.235-0.01×νd

式中：NWF2為B3+ 、Si4+ 及Al3+ 的合計含量；RE2為La3+ 、Gd3+ 、Y3+ 及Yb3+ 的合計含量；HR2為Nb5+ 、Ti4+ 、W6+ 及Bi3+ 的合計含量；D2=(Li+ +Na+ +K+ )×6+Zn2+ ；L2= (10×Li+ )+(8×Na+ )+(4×K+ )+(4×Zn+ )+Mg2+ +(2×Ca2+ )+(2×Sr2+ )+(2×Ba2+ )+B3+ +Nb5+ +Ti4+ +(4×W6+ )+(4×Bi3+ )+Ta5+ -(2×Si4+ )-Al3+ -(2×Zr4+ )-La3+ -Gd3+ -Y3+ -Yb3+ ；上述各成分的含量為以陽離子%表示的值。In the formula: NWF2 is the total content of B 3+ , Si 4+ and Al 3+ ; RE2 is the total content of La 3+ , Gd 3+ , Y 3+ and Yb 3+ ; HR2 is Nb 5+ , Ti 4+ , W 6+ and Bi 3+ total content; D2=(Li + +Na + +K + )×6+Zn 2+ ; L2=(10×Li + )+(8×Na + )+(4× K + )+(4×Zn + )+Mg 2+ +(2×Ca 2+ )+(2×Sr 2+ )+(2×Ba 2+ )+B 3+ +Nb 5+ +Ti 4+ +(4×W 6+ )+(4×Bi 3+ )+Ta 5+ -(2×Si 4+ )-Al 3+ -(2×Zr 4+ )-La 3+ -Gd 3+ -Y 3+ -Yb 3+ ; the content of each of the above components is a value expressed in cation %.

另外，在上述式中，表示為B3+ 、Si4+ 、Al3+ 、La3+ 、Gd3+ 、Y3+ 、Yb3+ 、Nb5+ 、Ti4+ 、W6+ 、Bi3+ 、Li+ 、Na+ 、K+ 、Zn+ 、Mg2+ 、Ca2+ 、Sr2+ 、Ba2+ 、Ta5+ 、Zr4+ 及La3+ 的各成分的含量為以陽離子%表示的各成分的含量。此外，L2、D2是關於本發明的光學玻璃中的特定的玻璃成分的含量的指標，僅由數值表示，不附加陽離子%或%。對於以下的記載也是同樣的。In addition, in the above formula, B 3+ , Si 4+ , Al 3+ , La 3+ , Gd 3+ , Y 3+ , Yb 3+ , Nb 5+ , Ti 4+ , W 6+ , Bi 3+ , Li + , Na + , K + , Zn + , Mg 2+ , Ca 2+ , Sr 2+ , Ba 2+ , Ta 5+ , Zr 4+ and La 3+ The content of each component expressed in %. In addition, L2 and D2 are indexes regarding the content of the specific glass component in the optical glass of this invention, and are only represented by numerical values, and cation % or % is not added. The same applies to the following description.

以下，對本實施形態的光學玻璃進行詳細說明。Hereinafter, the optical glass of this embodiment is demonstrated in detail.

本實施形態的光學玻璃的阿貝數(νd)為39.0以上、45.0以下，折射率(nd)與上述的阿貝數(νd)滿足下述式(1)。The Abbe number (νd) of the optical glass of the present embodiment is 39.0 or more and 45.0 or less, and the refractive index (nd) and the above-mentioned Abbe number (νd) satisfy the following formula (1).

式(1) nd≥2.235-0.01×νd 在本實施形態的光學玻璃中，阿貝數(νd)為39.0以上、45.0以下，阿貝數(νd)的下限較佳為39.5，更佳為40.0，進一步較佳為40.5。阿貝數(νd)的上限較佳為44.5，更佳為44.0，進一步較佳為43.5。Formula 1) nd≥2.235-0.01×νd In the optical glass of the present embodiment, the Abbe number (νd) is 39.0 or more and 45.0 or less, and the lower limit of the Abbe number (νd) is preferably 39.5, more preferably 40.0, and still more preferably 40.5. The upper limit of the Abbe number (νd) is preferably 44.5, more preferably 44.0, and still more preferably 43.5.

在本實施形態的光學玻璃中，上述NWF2、RE2、HR2意味著每100g玻璃所包含的特定陽離子的以陽離子%表示的合計含量。In the optical glass of the present embodiment, the above-mentioned NWF2, RE2, and HR2 mean the total content in terms of cation % of specific cations contained in 100 g of glass.

＜RE2/NWF2＞ 在本實施形態的光學玻璃中，NWF2是以陽離子%表示的網絡形成成分B3+ 、Si4+ 及Al3+ 的各含量的合計含量(NWF2=B3+ +Si4+ +Al3+ )。<RE2/NWF2> In the optical glass of the present embodiment, NWF2 is the total content of the respective contents of the network-forming components B 3+ , Si 4+ and Al 3+ represented by cation % (NWF2=B 3+ +Si 4 ). + +Al 3+ ).

此外，在本實施形態的光學玻璃中，RE2是以陽離子%表示的高折射率低色散化成分La3+ 、Gd3+ 、Y3+ 及Yb3+ 的各含量的合計含量(RE2=La3+ +Gd3+ +Y3+ +Yb3+ )。In addition, in the optical glass of the present embodiment, RE2 is the total content of each content of the high refractive index and low dispersion components La 3+ , Gd 3+ , Y 3+ and Yb 3+ represented by cation % (RE2=La 3+ +Gd 3+ +Y 3+ +Yb 3+ ).

在本實施形態的光學玻璃中，RE2相對於NWF2的比例，即陽離子比[RE2/NWF2]為0.35以上。In the optical glass of the present embodiment, the ratio of RE2 to NWF2, that is, the cation ratio [RE2/NWF2] is 0.35 or more.

在本實施形態的光學玻璃中，陽離子比[RE2/NWF2]的下限較佳為0.40。此外，陽離子比[RE2/NWF2]的上限較佳為0.55。In the optical glass of the present embodiment, the lower limit of the cation ratio [RE2/NWF2] is preferably 0.40. Further, the upper limit of the cation ratio [RE2/NWF2] is preferably 0.55.

在本實施形態的光學玻璃中，NWF2的上限較佳為0.74，更佳為0.72，進一步較佳為0.70，再進一步較佳為0.69。此外，NWF2的下限較佳為0.45，更佳為0.48，進一步較佳為0.50，再進一步較佳為0.51。In the optical glass of the present embodiment, the upper limit of NWF2 is preferably 0.74, more preferably 0.72, still more preferably 0.70, and still more preferably 0.69. In addition, the lower limit of NWF2 is preferably 0.45, more preferably 0.48, still more preferably 0.50, and still more preferably 0.51.

在本實施形態的光學玻璃中，RE2的上限較佳為31，更佳為29，進一步較佳為28，再進一步較佳為27。此外，RE2的下限較佳為19，更佳為21，進一步較佳為22，再進一步較佳為23。In the optical glass of the present embodiment, the upper limit of RE2 is preferably 31, more preferably 29, still more preferably 28, and still more preferably 27. In addition, the lower limit of RE2 is preferably 19, more preferably 21, still more preferably 22, and still more preferably 23.

＜HR2/RE2＞ 在本實施形態的光學玻璃中，HR2是以陽離子%表示的高折射率高色散化成分Nb5+ 、Ti4+ 、W6+ 及Bi3+ 的各含量的合計含量(HR2=Nb5+ +Ti4+ +W6+ +Bi3+ )。<HR2/RE2> In the optical glass of the present embodiment, HR2 is the total content of each of the high refractive index and high dispersion components Nb 5+ , Ti 4+ , W 6+ and Bi 3+ expressed as cation % ( HR2=Nb 5+ +Ti 4+ +W 6+ +Bi 3+ ).

在本實施形態的光學玻璃中，HR2相對於RE2的比例，即陽離子比[HR2/RE2]為0.33以下。In the optical glass of the present embodiment, the ratio of HR2 to RE2, that is, the cation ratio [HR2/RE2] is 0.33 or less.

在本實施形態的光學玻璃中，陽離子比[HR2/RE2]的上限較佳為0.32，進而依次更佳為0.31、0.30、0.29、0.28、0.27、0.25。此外，陽離子比[HR2/RE2]的下限較佳為0.04，進而依次更佳為0.08、0.10、0.11、0.13、0.15、0.16。In the optical glass of the present embodiment, the upper limit of the cation ratio [HR2/RE2] is preferably 0.32, and more preferably 0.31, 0.30, 0.29, 0.28, 0.27, and 0.25 in this order. Further, the lower limit of the cation ratio [HR2/RE2] is preferably 0.04, and more preferably 0.08, 0.10, 0.11, 0.13, 0.15, and 0.16 in this order.

從實現所需的折射率和阿貝數、提供適合於精密壓製成型的光學玻璃的觀點出發，陽離子比[HR2/RE2]較佳為上述範圍。The cation ratio [HR2/RE2] is preferably within the above-mentioned range from the viewpoint of realizing the desired refractive index and Abbe number and providing an optical glass suitable for precision press molding.

在本實施形態的光學玻璃中，HR2的上限較佳為9，進而依次更佳為8.0、7.5、7.0、6.5、6.0。此外，HR2的下限較佳為1，進而依次更佳為2.0、2.5、3.0、3.5、4.0。In the optical glass of the present embodiment, the upper limit of HR2 is preferably 9, and more preferably 8.0, 7.5, 7.0, 6.5, and 6.0 in this order. Further, the lower limit of HR2 is preferably 1, and more preferably 2.0, 2.5, 3.0, 3.5, and 4.0 in this order.

＜Nb5+ /(Nb5+ +Ta5+ )＞ 在本實施形態的光學玻璃中，Nb5+ 的含量相對於Nb5+ 和Ta5+ 的合計含量的比例，即陽離子比[Nb5+ /(Nb5+ +Ta5+ )]為3/4以上。<Nb 5+ /(Nb 5+ +Ta 5+ )> In the optical glass of the present embodiment, the ratio of the content of Nb 5+ to the total content of Nb 5+ and Ta 5+ , that is, the cation ratio [Nb 5+ + /(Nb 5+ +Ta 5+ )] is 3/4 or more.

在本實施形態的光學玻璃中，陽離子比[Nb5+ /(Nb5+ +Ta5+ )]的下限較佳為0.76，進而依次更佳為0.78、0.80、0.85、0.90、0.95、0.97、0.99、1。此外，陽離子比[Nb5+ /(Nb5+ +Ta5+ )]的上限較佳為1。另外，陽離子比[Nb5+ /(Nb5+ +Ta5+ )]也可以為1。In the optical glass of the present embodiment, the lower limit of the cation ratio [Nb 5+ /(Nb 5+ +Ta 5+ )] is preferably 0.76, more preferably 0.78, 0.80, 0.85, 0.90, 0.95, 0.97, 0.99, 1. Further, the upper limit of the cation ratio [Nb 5+ /(Nb 5+ +Ta 5+ )] is preferably 1. In addition, the cation ratio [Nb 5+ /(Nb 5+ +Ta 5+ )] may be 1.

＜RE2/D2＞ 在本實施形態的光學玻璃中，D2是以陽離子%表示的更容易揮發的Li+ 、Na+ 及K+ 的各含量的值乘以6的值與以陽離子%表示的易揮發的Zn2+ 的含量的值的合計值(D2=(Li+ ×6)+(Na+ ×6)+(K+ ×6)+Zn2+ )。即，D2能夠表示為D2=(Li+ +Na+ +K+ )×6+Zn2+ 。D2是關於本發明的光學玻璃中的揮發性成分的含量的指標，僅由數值表示。<RE2/D2> In the optical glass of the present embodiment, D2 is a value obtained by multiplying the value of each content of Li + , Na + , and K + which are more easily volatile in cation % by 6 and the cation % in %. The total value of the content of volatilized Zn 2+ (D2=(Li + ×6)+(Na + ×6)+(K + ×6)+Zn 2+ ). That is, D2 can be expressed as D2=(Li + +Na + +K + )×6+Zn 2+ . D2 is an index regarding the content of the volatile component in the optical glass of the present invention, and is only represented by a numerical value.

D2是對促進將玻璃熔融時的揮發的因數進行數值化的值，RE2是對抑制將玻璃熔融時的揮發的因數進行數值化的值。即，比[RE2/D2]為表示玻璃熔液的揮發性的指標。D2 is a numerical value of a factor that promotes volatilization at the time of melting glass, and RE2 is a numerical value of a factor that suppresses volatilization at the time of melting glass. That is, the ratio [RE2/D2] is an index showing the volatility of the molten glass.

因此，在本實施形態的光學玻璃中，比[RE2/D2]為0.90以上。Therefore, in the optical glass of this embodiment, ratio [RE2/D2] is 0.90 or more.

在本實施形態的光學玻璃中，比[RE2/D2]的下限較佳為0.95，進而依次更佳為1.00、1.05、1.10、1.15、1.20。此外，比[RE2/D2]的上限較佳為5，進而依次更佳為4、3、2.7、2.5、2.4。In the optical glass of the present embodiment, the lower limit of the ratio [RE2/D2] is preferably 0.95, and more preferably 1.00, 1.05, 1.10, 1.15, and 1.20 in this order. Further, the upper limit of the ratio [RE2/D2] is preferably 5, and more preferably 4, 3, 2.7, 2.5, and 2.4 in this order.

藉由將比[RE2/D2]設為0.90以上，從而能夠抑制熔融玻璃即玻璃熔液的揮發。其結果是，能夠穩定地生產具有所需的特性的光學玻璃。此外，還能夠保持玻璃的高均質性。另一方面，藉由將比[RE2/D2]的上限設為5，從而能夠改善玻璃的熔融性，並且能夠抑制玻璃化轉變溫度Tg的上升，能夠藉由精密壓製成型穩定地製造高質量的玻璃制的光學元件。By making ratio [RE2/D2] 0.90 or more, volatilization of molten glass, ie, molten glass, can be suppressed. As a result, optical glass having desired properties can be stably produced. In addition, the high homogeneity of the glass can be maintained. On the other hand, by setting the upper limit of the ratio [RE2/D2] to 5, the meltability of the glass can be improved, the rise of the glass transition temperature Tg can be suppressed, and the high-quality glass can be stably produced by precision press molding. Optical elements made of glass.

＜L2/(NWF2+RE2)＞ 將玻璃成分大致分為具有使玻璃化轉變溫度(Tg)相對降低的作用的成分和具有使玻璃化轉變溫度(Tg)相對上升的作用的成分。具有使玻璃化轉變溫度Tg相對降低的作用的成分主要為Li+ 、Na+ 、K+ 、Zn2+ 、Mg2+ 、Ca2+ 、Sr2+ 、Ba2+ 、B3+ 、Nb5+ 、Ti4+ 、W6+ 、Bi3+ 、Ta5+ 。另一方面，相對於上述玻璃成分，具有使玻璃化轉變溫度Tg相對上升的作用的成分主要為Si4+ 、Al3+ 、Zr4+ 、La3+ 、Gd3+ 、Y3+ 、Yb3+ 。<L2/(NWF2+RE2)> The glass components are roughly classified into those having an action of relatively lowering the glass transition temperature (Tg) and those having an action of relatively increasing the glass transition temperature (Tg). The components having the effect of relatively lowering the glass transition temperature Tg are mainly Li + , Na + , K + , Zn 2+ , Mg 2+ , Ca 2+ , Sr 2+ , Ba 2+ , B 3+ , and Nb 5 . + , Ti 4+ , W 6+ , Bi 3+ , Ta 5+ . On the other hand, the components having the effect of relatively increasing the glass transition temperature Tg relative to the above-mentioned glass components are mainly Si 4+ , Al 3+ , Zr 4+ , La 3+ , Gd 3+ , Y 3+ , and Yb 3+ .

本申請發明人進行研究的結果發現，L2相對於NWF2和RE2的合計值的比[L2/(NWF2+RE2)]與玻璃化轉變溫度Tg之間存在相關關係，其中，L2是對以陽離子%表示的上述成分的各含量的值分別作為係數乘以各成分對玻璃化轉變溫度(Tg)的影響度的值的合計值。另外，在表4示出表示以陽離子比為基準的上述成分對玻璃化轉變溫度Tg的影響度的係數。As a result of research conducted by the inventors of the present application, it was found that there is a correlation between the ratio of L2 to the total value of NWF2 and RE2 [L2/(NWF2+RE2)] and the glass transition temperature Tg, where L2 is the ratio of cation % The indicated value of each content of the above-mentioned components is taken as the total value of the value obtained by multiplying the influence degree of each component on the glass transition temperature (Tg) by the coefficient. Moreover, in Table 4, the coefficient which shows the influence degree of the said component on the glass transition temperature Tg based on a cation ratio is shown.

[表4] 玻璃成分 係數 玻璃成分 係數 玻璃成分 係數 Li+ +10 Ba2+ +2 Bi3+ +4 Na+ +8 B3+ +1 Ta5+ +1 K+ +4 Si4+ -2 Zr4+ -2 Zn2+ +4 Al3+ -1 La3+ -1 Mg2+ +1 Nb5+ +1 Gd3+ -1 Ca2+ +2 Ti4+ +1 Y3+ -1 Sr2+ +2 W6+ +4 Yb3+ -1 [Table 4] glass composition coefficient glass composition coefficient glass composition coefficient Li + +10 Ba 2+ +2 Bi 3+ +4 Na + +8 B 3+ +1 Ta 5+ +1 K + +4 Si 4+ -2 Zr 4+ -2 Zn 2+ +4 Al 3+ -1 La 3+ -1 Mg 2+ +1 Nb 5+ +1 Gd 3+ -1 Ca 2+ +2 Ti 4+ +1 Y 3+ -1 Sr 2+ +2 W 6+ +4 Yb 3+ -1

這樣的L2能夠表示為L2=(10×Li+ )+(8×Na+ )+(4× K+ )+(4×Zn+ )+(1×Mg2+ )+(2×Ca2+ )+(2×Sr2+ )+(2×Ba2+ )+(1×B3+ )+(1×Nb5+ )+(1×Ti4+ )+(4×W6+ )+(4×Bi3+ )+(1×Ta5+ )+(-2×Si4+ )+(-1×Al3+ )+(-2×Zr4+ )+(-1×La3+ )+(-1×Gd3+ )+(-1×Y3+ )+(-1×Yb3+ )。Such L2 can be expressed as L2=(10×Li + )+(8×Na + )+(4×K + )+(4×Zn + )+(1×Mg 2+ )+(2×Ca 2+ )+(2×Sr 2+ )+(2×Ba 2+ )+(1×B 3+ )+(1×Nb 5+ )+(1×Ti 4+ )+(4×W 6+ )+ (4×Bi 3+ )+(1×Ta 5+ )+(-2×Si 4+ )+(-1×Al 3+ )+(-2×Zr 4+ )+(-1×La 3+ )+(−1×Gd 3+ )+(−1×Y 3+ )+(−1×Yb 3+ ).

即，L2能夠表示為L2=(10×Li+ )+(8×Na+ )+(4×K+ )+ (4×Zn+ )+Mg2+ +(2×Ca2+ )+(2×Sr2+ )+(2×Ba2+ )+B3+ +Nb5+ +Ti4+ +(4×W6+ )+(4×Bi3+ )+Ta5+ -(2×Si4+ )-Al3+ -(2×Zr4+ )-La3+ -Gd3+ -Y3+ -Yb3+ 。That is, L2 can be expressed as L2=(10×Li + )+(8×Na + )+(4×K + )+ (4×Zn + )+Mg 2+ +(2×Ca 2+ )+(2 ×Sr 2+ )+(2×Ba 2+ )+B 3+ +Nb 5+ +Ti 4+ +(4×W 6+ )+(4×Bi 3+ )+Ta 5+ -(2×Si 4+ )-Al 3+ -(2×Zr 4+ )-La 3+ -Gd 3+ -Y 3+ -Yb 3+ .

圖2是將橫軸設為L2相對於NWF2與RE2的合計值的比[L2/(NWF2+RE2)]及將縱軸設為玻璃化轉變溫度(Tg)而對公知的玻璃繪製了比[L2/(NWF2+RE2)]和玻璃化轉變溫度(Tg)的圖，其中，NWF2是玻璃成分中網絡形成成分的合計含量，RE2稀土類離子的合計含量。從圖2可明確地看出，點基本分佈在直線上，可知比[L2/(NWF2+RE2)]與玻璃化轉變溫度(Tg)存在相關關係。Fig. 2 plots the ratio [L2/(NWF2+RE2)] of L2 to the total value of NWF2 and RE2 on the horizontal axis and the glass transition temperature (Tg) on the vertical axis for a known glass [ L2/(NWF2+RE2)] and a graph of glass transition temperature (Tg), where NWF2 is the total content of network-forming components in the glass component, and RE2 is the total content of rare earth ions. It can be clearly seen from FIG. 2 that the points are basically distributed on a straight line, and it can be seen that there is a correlation between the ratio [L2/(NWF2+RE2)] and the glass transition temperature (Tg).

即，隨著比[L2/(NWF2+RE2)]的增加，玻璃化轉變溫度(Tg)降低，隨著比[L2/(NWF2+RE2)]的減小，玻璃化轉變溫度(Tg)上升。That is, as the ratio [L2/(NWF2+RE2)] increases, the glass transition temperature (Tg) decreases, and as the ratio [L2/(NWF2+RE2)] decreases, the glass transition temperature (Tg) increases .

像這樣，藉由使比[L2/(NWF2+RE2)]增加，從而能夠使玻璃化轉變溫度(Tg)降低，能夠提供適合於精密壓製成型的玻璃，即，能夠提供具有低溫軟化性的玻璃。此外，藉由使比[L2/(NWF2+RE2)]增加，從而可改善玻璃的熔融性。即，玻璃原料不會產生熔融殘留，能夠提供均質的玻璃。As described above, by increasing the ratio [L2/(NWF2+RE2)], the glass transition temperature (Tg) can be lowered, and glass suitable for precision press molding, that is, glass having low-temperature softening properties can be provided. . Further, by increasing the ratio [L2/(NWF2+RE2)], the meltability of the glass can be improved. That is, a homogeneous glass can be provided without generating molten residues in the glass raw material.

在本實施形態的光學玻璃中，比[L2/(NWF2+RE2)]為0.78以上。In the optical glass of the present embodiment, the ratio [L2/(NWF2+RE2)] is 0.78 or more.

在本實施形態的光學玻璃中，比[L2/(NWF2+RE2)]的下限較佳為0.80，進而依次更佳為0.85、0.90、0.95、1.00、1.05。In the optical glass of the present embodiment, the lower limit of the ratio [L2/(NWF2+RE2)] is preferably 0.80, and more preferably 0.85, 0.90, 0.95, 1.00, and 1.05 in this order.

從得到適合於精密壓製成型的低溫軟化性並且改善玻璃的熔融性的觀點出發，較佳比[L2/(NWF2+RE2)]的下限為上述範圍。The lower limit of the preferable ratio [L2/(NWF2+RE2)] is the above-mentioned range from the viewpoint of obtaining low-temperature softening properties suitable for precision press molding and improving the meltability of glass.

＜玻璃組成＞ 以下，對玻璃組成進行詳細說明。另外，只要沒有特別說明，各種玻璃構成成分(玻璃成分)的含量等以陽離子%或陰離子%表示。本實施形態的光學玻璃為氧化物玻璃，藉由確定陽離子成分的含有比率(含量)，從而能夠確定玻璃組成。＜Glass composition＞ Hereinafter, the glass composition will be described in detail. In addition, unless otherwise specified, the content and the like of various glass constituent components (glass components) are represented by cation % or anion %. The optical glass of the present embodiment is oxide glass, and the glass composition can be determined by determining the content ratio (content) of the cationic component.

在本實施形態的光學玻璃中，B3+ 的含量的上限較佳為65%，進而依次更佳為62%、60%、57%、56%、55%。此外，B3+ 的含量的下限較佳為40%，進而依次更佳為43%、45%、46%、47%、48%。In the optical glass of the present embodiment, the upper limit of the content of B 3+ is preferably 65%, and more preferably 62%, 60%, 57%, 56%, and 55% in this order. In addition, the lower limit of the content of B 3+ is preferably 40%, and more preferably 43%, 45%, 46%, 47%, and 48% in this order.

在本實施形態的光學玻璃中，Si4+ 的含量的上限較佳為10%，進而依次更佳為8%、7%、6%、5%。此外，Si4+ 的含量的下限較佳為0%。另外，Si4+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Si 4+ is preferably 10%, and more preferably 8%, 7%, 6%, and 5% in this order. Further, the lower limit of the content of Si 4+ is preferably 0%. In addition, the content of Si 4+ may be 0%.

在本實施形態的光學玻璃中，Al3+ 的含量的上限較佳為10%，進而依次更佳為7%、5%、4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Al3+ 的含量的下限較佳為0%。另外，Al3+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Al 3+ is preferably 10%, and more preferably 7%, 5%, 4%, 3%, 2.5%, 2%, 1.5%, and 1% in this order. , 0.5%, 0.1%, 0.05%. Further, the lower limit of the content of Al 3+ is preferably 0%. In addition, the content of Al 3+ may be 0%.

在本實施形態的光學玻璃中，B3+ 、Si4+ 及Al3+ 的合計含量[B3+ +Si4+ +Al3+ ]的上限較佳為62，進而依次更佳為60、58、56、55。合計含量[B3+ +Si4+ +Al3+ ]的下限較佳為40，進而依次更佳為43、45、46、48。In the optical glass of the present embodiment, the upper limit of the total content of B 3+ , Si 4+ and Al 3+ [B 3+ +Si 4+ +Al 3+ ] is preferably 62, more preferably 60, 58, 56, 55. The lower limit of the total content [B 3+ +Si 4+ +Al 3+ ] is preferably 40, and more preferably 43, 45, 46, and 48 in this order.

在本實施形態的光學玻璃中，B3+ 的含量相對於B3+ 、Si4+ 及Al3+ 的合計含量[B3+ +Si4+ +Al3+ ]的比例，即陽離子比[B3+ /(B3+ +Si4+ +Al3+ )]的上限較佳為1。此外，陽離子比[B3+ /(B3+ +Si4+ +Al3+ )]的下限較佳為0.70，進而依次更佳為0.75、0.80、0.85、0.88、0.90。另外，陽離子比[B3+ /(B3+ +Si4+ +Al3+ )]也可以為1。In the optical glass of the present embodiment, the ratio of the content of B 3+ to the total content of B 3+ , Si 4+ and Al 3+ [B 3+ +Si 4+ +Al 3+ ], that is, the cation ratio [ The upper limit of B 3+ /(B 3+ +Si 4+ +Al 3+ )] is preferably 1. Further, the lower limit of the cation ratio [B 3+ /(B 3+ +Si 4+ +Al 3+ )] is preferably 0.70, and more preferably 0.75, 0.80, 0.85, 0.88, and 0.90 in this order. In addition, the cation ratio [B 3+ /(B 3+ +Si 4+ +Al 3+ )] may be 1.

在本實施形態的光學玻璃中，La3+ 、Gd3+ 、Y3+ 及Yb3+ 的合計含量[La3+ +Gd3+ +Y3+ +Yb3+ ]的上限較佳為35%，進而依次更佳為30%、28%、27%。此外，合計含量[La3+ +Gd3+ +Y3+ +Yb3+ ]的下限較佳為16%，進而依次更佳為18%、20%、21%、22%、23%。In the optical glass of the present embodiment, the upper limit of the total content of La 3+ , Gd 3+ , Y 3+ and Yb 3+ [La 3+ +Gd 3+ +Y 3+ +Yb 3+ ] is preferably 35 %, and more preferably 30%, 28%, and 27% in this order. Further, the lower limit of the total content [La 3+ +Gd 3+ +Y 3+ +Yb 3+ ] is preferably 16%, and more preferably 18%, 20%, 21%, 22%, and 23% in this order.

在本實施形態的光學玻璃中，La3+ 的含量的上限較佳為27%，進而依次更佳為25%、23%、22%、21%、20%、19%。此外，La3+ 的含量的下限較佳為5%，進而依次更佳為8%、9%、10%、11%。In the optical glass of the present embodiment, the upper limit of the content of La 3+ is preferably 27%, and more preferably 25%, 23%, 22%, 21%, 20%, and 19% in this order. In addition, the lower limit of the content of La 3+ is preferably 5%, and more preferably 8%, 9%, 10%, and 11% in this order.

在本實施形態的光學玻璃中，Gd3+ 的含量的上限較佳為22%，進而依次更佳為20%、18%、15%、14%、13%。此外，Gd3+ 的含量的下限較佳為1%，進而依次更佳為2%、3%、4%、5%。In the optical glass of the present embodiment, the upper limit of the content of Gd 3+ is preferably 22%, and more preferably 20%, 18%, 15%, 14%, and 13% in this order. In addition, the lower limit of the content of Gd 3+ is preferably 1%, and more preferably 2%, 3%, 4%, and 5% in this order.

在本實施形態的光學玻璃中，Y3+ 的含量的上限較佳為15%，進而依次更佳為12%、10%、8%、5%、4%、3%。此外，Y3+ 的含量的下限較佳為0%。In the optical glass of the present embodiment, the upper limit of the content of Y 3+ is preferably 15%, and more preferably 12%, 10%, 8%, 5%, 4%, and 3% in this order. Further, the lower limit of the content of Y 3+ is preferably 0%.

在本實施形態的光學玻璃中，Yb3+ 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.3%、0.2%、0.1%、0.05%、0.01%。此外，Yb3+ 的含量的下限較佳為0%。另外，Yb3+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Yb 3+ is preferably 5%, and more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.3% in this order. , 0.2%, 0.1%, 0.05%, 0.01%. Further, the lower limit of the content of Yb 3+ is preferably 0%. In addition, the content of Yb 3+ may be 0%.

在本實施形態的光學玻璃中，La3+ 的含量相對於La3+ 、Gd3+ 、Y3+ 及Yb3+ 的合計含量[La3+ +Gd3+ +Y3+ +Yb3+ ]的比例，即陽離子比[La3+ /(La3+ +Gd3+ +Y3+ +Yb3+ )]的上限較佳為0.99，進而依次更佳為0.97、0.95、0.93、0.90、0.85、0.80、0.77、0.76、0.75。此外，陽離子比[La3+ /(La3+ +Gd3+ +Y3+ +Yb3+ )]的下限較佳為0.3，進而依次更佳為0.4、0.45、0.46、0.47、0.48。藉由使陽離子比[La3+ /(La3+ +Gd3+ +Y3+ +Yb3+ )]為上述範圍，從而能夠改善熱穩定性和熔融性。In the optical glass of the present embodiment, the content of La 3+ relative to the total content of La 3+ , Gd 3+ , Y 3+ and Yb 3+ [La 3+ +Gd 3+ +Y 3+ +Yb 3+ ], that is, the upper limit of the cation ratio [La 3+ /(La 3+ +Gd 3+ +Y 3+ +Yb 3+ )] is preferably 0.99, and more preferably 0.97, 0.95, 0.93, 0.90, 0.85, 0.80, 0.77, 0.76, 0.75. Further, the lower limit of the cation ratio [La 3+ /(La 3+ +Gd 3+ +Y 3+ +Yb 3+ )] is preferably 0.3, and more preferably 0.4, 0.45, 0.46, 0.47, and 0.48 in this order. By making the cation ratio [La 3+ /(La 3+ +Gd 3+ +Y 3+ +Yb 3+ )] within the above range, thermal stability and meltability can be improved.

在本實施形態的光學玻璃中，La3+ 、Gd3+ 、Y3+ 及Yb3+ 的合計含量[La3+ +Gd3+ +Y3+ +Yb3+ ]相對於B3+ 、Si4+ 及Al3+ 的合計含量[B3+ +Si4+ +Al3+ ]的比例，即陽離子比[(La3+ +Gd3+ +Y3+ +Yb3+ )/(B3+ +Si4+ +Al3+ )]的上限較佳為0.80，進而依次更佳為0.70、0.60、0.55、0.52、0.51。此外，陽離子比[(La3+ +Gd3+ +Y3+ +Yb3+ )/(B3+ +Si4+ +Al3+ )]的下限較佳為0.35，進而依次更佳為0.36、0.37、0.38、0.39、0.40、0.41、0.42、0.43。In the optical glass of the present embodiment, the total content of La 3+ , Gd 3+ , Y 3+ and Yb 3+ [La 3+ +Gd 3+ +Y 3+ +Yb 3+ ] relative to B 3+ , The ratio of the total content of Si 4+ and Al 3+ [B 3+ +Si 4+ +Al 3+ ], that is, the cation ratio [(La 3+ +Gd 3+ +Y 3+ +Yb 3+ )/(B The upper limit of 3+ +Si 4+ +Al 3+ )] is preferably 0.80, and more preferably 0.70, 0.60, 0.55, 0.52, and 0.51 in this order. Further, the lower limit of the cation ratio [(La 3+ +Gd 3+ +Y 3+ +Yb 3+ )/(B 3+ +Si 4+ +Al 3+ )] is preferably 0.35, more preferably 0.36 in this order , 0.37, 0.38, 0.39, 0.40, 0.41, 0.42, 0.43.

在本實施形態的光學玻璃中，Zn2+ 的含量的上限較佳為25%，進而依次更佳為22%、20%、18%、17%、16%、15%。此外，Zn2+ 的含量的下限較佳為5%，進而更佳為8%、9%、10%、11%、12%。In the optical glass of the present embodiment, the upper limit of the content of Zn 2+ is preferably 25%, and more preferably 22%, 20%, 18%, 17%, 16%, and 15% in this order. In addition, the lower limit of the content of Zn 2+ is preferably 5%, and more preferably 8%, 9%, 10%, 11%, and 12%.

在本實施形態的光學玻璃中，Zr4+ 的含量的上限較佳為9%，進而依次更佳為8%、7%、6%、5%、4.5%、4%。此外，Zr4+ 的含量的下限較佳為0%，進而依次更佳為0.1%、0.5%、1%、1.5%、2%、2.5%。In the optical glass of the present embodiment, the upper limit of the content of Zr 4+ is preferably 9%, and more preferably 8%, 7%, 6%, 5%, 4.5%, and 4% in this order. Further, the lower limit of the content of Zr 4+ is preferably 0%, and more preferably 0.1%, 0.5%, 1%, 1.5%, 2%, and 2.5% in this order.

在本實施形態的光學玻璃中，Nb5+ 的含量的上限較佳為9%，進而依次更佳為8%、7%、6%、5%、4.5%、4%。此外，Nb5+ 的含量的下限較佳為0.1%，進而依次更佳為0.2%、0.3%、0.5%、1%、2%。In the optical glass of the present embodiment, the upper limit of the content of Nb 5+ is preferably 9%, and more preferably 8%, 7%, 6%, 5%, 4.5%, and 4% in this order. In addition, the lower limit of the content of Nb 5+ is preferably 0.1%, and more preferably 0.2%, 0.3%, 0.5%, 1%, and 2% in this order.

在本實施形態的光學玻璃中，Ta5+ 的含量的上限較佳為3%，進而依次更佳為2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Ta5+ 的含量的下限較佳為0%。另外，Ta5+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Ta 5+ is preferably 3%, and more preferably 2.5%, 2%, 1.5%, 1%, 0.5%, 0.1%, and 0.05% in this order. Moreover, the lower limit of the content of Ta 5+ is preferably 0%. In addition, the content of Ta 5+ may be 0%.

在本實施形態的光學玻璃中，Nb5+ 、Ti4+ 、W6+ 及Bi3+ 的合計含量[Nb5+ +Ti4+ +W6+ +Bi3+ ]的上限較佳為10%，進而更佳為9.0%、8.0%、7.0%、6.5%、6.0%。此外，合計含量[Nb5+ +Ti4+ +W6+ +Bi3+ ]的下限較佳為0.1%，進而更佳為0.2%、0.3%、0.5%、1%、1.5%、2%、2.5%、3%。In the optical glass of the present embodiment, the upper limit of the total content of Nb 5+ , Ti 4+ , W 6+ and Bi 3+ [Nb 5+ +Ti 4+ +W 6+ +Bi 3+ ] is preferably 10 %, and more preferably 9.0%, 8.0%, 7.0%, 6.5%, 6.0%. In addition, the lower limit of the total content [Nb 5+ +Ti 4+ +W 6+ +Bi 3+ ] is preferably 0.1%, more preferably 0.2%, 0.3%, 0.5%, 1%, 1.5%, 2% , 2.5%, 3%.

在本實施形態的光學玻璃中，Ti4+ 、W6+ 及Bi3+ 的合計含量[Ti4+ +W6+ +Bi3+ ]的上限較佳為6%，進而依次更佳為5.5%、5%、4.5%、4%。此外，合計含量[Ti4+ +W6+ +Bi3+ ]的下限較佳為0%，進而依次更佳為0.05%、0.1%、0.5%、1.0%、1.5%、2.0%。In the optical glass of the present embodiment, the upper limit of the total content of Ti 4+ , W 6+ and Bi 3+ [Ti 4+ +W 6+ +Bi 3+ ] is preferably 6%, more preferably 5.5 %, 5%, 4.5%, 4%. Further, the lower limit of the total content [Ti 4+ +W 6+ +Bi 3+ ] is preferably 0%, and more preferably 0.05%, 0.1%, 0.5%, 1.0%, 1.5%, and 2.0% in this order.

在本實施形態的光學玻璃中，W6+ 的含量的上限較佳為6%，進而依次更佳為5%、4%。此外，W6+ 的含量的下限較佳為0%，進而依次更佳為0.1%、0.5%、0.8%、1%、1.5%。另外，W6+ 的含量也可以為0%。此外，為了得到W6+ 的抑制玻璃化轉變溫度Tg上升的效果，也可以將W6+ 的含量設為0.5%以上。In the optical glass of the present embodiment, the upper limit of the content of W 6+ is preferably 6%, and more preferably 5% and 4% in this order. In addition, the lower limit of the content of W 6+ is preferably 0%, and more preferably 0.1%, 0.5%, 0.8%, 1%, and 1.5% in this order. In addition, the content of W 6+ may be 0%. In addition, in order to obtain the effect of suppressing the increase in the glass transition temperature Tg of W 6+ , the content of W 6+ may be 0.5% or more.

在本實施形態的光學玻璃中，Ti4+ 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Ti4+ 的含量的下限較佳為0%。另外，Ti4+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Ti 4+ is preferably 5%, and more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. , 0.05%. Further, the lower limit of the content of Ti 4+ is preferably 0%. In addition, the content of Ti 4+ may be 0%.

在本實施形態的光學玻璃中，Bi3+ 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Bi3+ 的含量的下限較佳為0%。另外，Bi3+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Bi 3+ is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. , 0.05%. Further, the lower limit of the content of Bi 3+ is preferably 0%. In addition, the content of Bi 3+ may be 0%.

在本實施形態的光學玻璃中，Li+ 的含量的上限較佳為10%，進而依次更佳為8%、6%、5%、4%、3%、2.5%。此外，Li+ 的含量的下限較佳為0%。另外，Li+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the Li + content is preferably 10%, and more preferably 8%, 6%, 5%, 4%, 3%, and 2.5% in this order. In addition, the lower limit of the content of Li + is preferably 0%. In addition, the content of Li + may be 0%.

在本實施形態的光學玻璃中，Na+ 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Na+ 的含量的下限較佳為0%。另外，Na+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Na + is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, 0.1%, 0.05%. Further, the lower limit of the content of Na + is preferably 0%. In addition, the content of Na + may be 0%.

在本實施形態的光學玻璃中，K+ 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，K+ 的含量的下限較佳為0%。另外，K+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of K + is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, 0.1%, 0.05%. Further, the lower limit of the content of K + is preferably 0%. In addition, the content of K + may be 0%.

在本實施形態的光學玻璃中，Li+ 、Na+ 及K+ 的合計含量[Li+ +Na+ +K+ ]的上限較佳為10%，進而依次更佳為8%、6%、5%、4%、3.5%、3%。此外，合計含量[Li+ +Na+ +K+ ]的下限較佳為0%。另外，合計含量[Li+ +Na+ +K+ ]也可以為0%。In the optical glass of the present embodiment, the upper limit of the total content of Li + , Na + and K + [Li + +Na + +K + ] is preferably 10%, more preferably 8%, 6%, and 5% in this order. %, 4%, 3.5%, 3%. Further, the lower limit of the total content [Li + +Na + +K + ] is preferably 0%. In addition, the total content [Li + +Na + +K + ] may be 0%.

在本實施形態的光學玻璃中，Rb+ 的含量的上限較佳為3%，進而依次更佳為2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Rb+ 的含量的下限較佳為0%。另外，Rb+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Rb + is preferably 3%, and more preferably 2.5%, 2%, 1.5%, 1%, 0.5%, 0.1%, and 0.05% in this order. Further, the lower limit of the content of Rb + is preferably 0%. In addition, the content of Rb + may be 0%.

在本實施形態的光學玻璃中，Cs+ 的含量的上限較佳為3%，進而依次更佳為2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Cs+ 的含量的下限較佳為0%。另外，Cs+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Cs + is preferably 3%, and more preferably 2.5%, 2%, 1.5%, 1%, 0.5%, 0.1%, and 0.05% in this order. In addition, the lower limit of the content of Cs + is preferably 0%. In addition, the content of Cs + may be 0%.

在本實施形態的光學玻璃中，Mg2+ 的含量的上限較佳為10%，進而依次更佳為7%、5%、4%、3%、2%、1.5%、1%、0.5%、0.1%。此外，Mg2+ 的含量的下限較佳為0%。另外，Mg2+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Mg 2+ is preferably 10%, and more preferably 7%, 5%, 4%, 3%, 2%, 1.5%, 1%, and 0.5% in this order. , 0.1%. Further, the lower limit of the content of Mg 2+ is preferably 0%. In addition, the content of Mg 2+ may be 0%.

在本實施形態的光學玻璃中，Ca2+ 的含量的上限較佳為10%，進而依次更佳為7%、5%、4%、3%、2%、1.5%、1%、0.5%、0.1%。此外，Ca2+ 的含量的下限較佳為0%。另外，Ca2+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Ca 2+ is preferably 10%, more preferably 7%, 5%, 4%, 3%, 2%, 1.5%, 1%, and 0.5% in this order. , 0.1%. Further, the lower limit of the content of Ca 2+ is preferably 0%. In addition, the content of Ca 2+ may be 0%.

在本實施形態的光學玻璃中，Sr2+ 的含量的上限較佳為10%，進而依次更佳為7%、5%、4%、3%、2%、1.5%、1%、0.5%、0.1%。此外，Sr2+ 的含量的下限較佳為0%。另外，Sr2+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Sr 2+ is preferably 10%, and more preferably 7%, 5%, 4%, 3%, 2%, 1.5%, 1%, and 0.5% in this order. , 0.1%. Further, the lower limit of the content of Sr 2+ is preferably 0%. In addition, the content of Sr 2+ may be 0%.

在本實施形態的光學玻璃中，Ba2+ 的含量的上限較佳為10%，進而依次更佳為7%、5%、4%、3%、2%、1.5%、1%、0.5%、0.1%。此外，Ba2+ 的含量的下限較佳為0%。另外，Ba2+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Ba 2+ is preferably 10%, and more preferably 7%, 5%, 4%, 3%, 2%, 1.5%, 1%, and 0.5% in this order. , 0.1%. Further, the lower limit of the content of Ba 2+ is preferably 0%. In addition, the content of Ba 2+ may be 0%.

在本實施形態的光學玻璃中，Mg2+ 、Ca2+ 、Sr2+ 及Ba2+ 的合計含量[Mg2+ +Ca2+ +Sr2+ +Ba2+ ]的上限較佳為10%，進而依次更佳為7%、5%、4%、3%、2%、1.5%、1%、0.5%、0.1%。此外，合計含量[Mg2+ +Ca2+ +Sr2+ +Ba2+ ]的下限較佳為0%。另外，合計含量[Mg2+ +Ca2+ +Sr2+ +Ba2+ ]也可以為0%。In the optical glass of the present embodiment, the upper limit of the total content of Mg 2+ , Ca 2+ , Sr 2+ and Ba 2+ [Mg 2+ +Ca 2+ +Sr 2+ +Ba 2+ ] is preferably 10 %, and more preferably 7%, 5%, 4%, 3%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. Further, the lower limit of the total content [Mg 2+ +Ca 2+ +Sr 2+ +Ba 2+ ] is preferably 0%. In addition, the total content [Mg 2+ +Ca 2+ +Sr 2+ +Ba 2+ ] may be 0%.

在本實施形態的光學玻璃中，Ga3+ 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Ga3+ 的含量的下限較佳為0%。另外，Ga3+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Ga 3+ is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. , 0.05%. Further, the lower limit of the content of Ga 3+ is preferably 0%. In addition, the content of Ga 3+ may be 0%.

在本實施形態的光學玻璃中，In3+ 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，In3+ 的含量的下限較佳為0%。另外，In3+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of In 3+ is preferably 5%, and more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. , 0.05%. Moreover, the lower limit of the content of In 3+ is preferably 0%. In addition, the content of In 3+ may be 0%.

在本實施形態的光學玻璃中，Sc3+ 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Sc3+ 的含量的下限較佳為0%。另外，Sc3+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Sc 3+ is preferably 5%, and more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. , 0.05%. Further, the lower limit of the content of Sc 3+ is preferably 0%. In addition, the content of Sc 3+ may be 0%.

在本實施形態的光學玻璃中，Hf4+ 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Hf4+ 的含量的下限較佳為0%。另外，Hf4+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Hf 4+ is preferably 5%, and more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. , 0.05%. Further, the lower limit of the content of Hf 4+ is preferably 0%. In addition, the content of Hf 4+ may be 0%.

在本實施形態的光學玻璃中，Lu3+ 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Lu3+ 的含量的下限較佳為0%。另外，Lu3+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Lu 3+ is preferably 5%, and more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. , 0.05%. Further, the lower limit of the content of Lu 3+ is preferably 0%. In addition, the content of Lu 3+ may be 0%.

在本實施形態的光學玻璃中，Ge4+ 的含量的上限較佳為5%，進而依次更佳為4%、3%、2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Ge4+ 的含量的下限較佳為0%。另外，Ge4+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Ge 4+ is preferably 5%, more preferably 4%, 3%, 2.5%, 2%, 1.5%, 1%, 0.5%, and 0.1% in this order. , 0.05%. Further, the lower limit of the content of Ge 4+ is preferably 0%. In addition, the content of Ge 4+ may be 0%.

此外，在本實施形態的光學玻璃中，P5+ 的含量的上限較佳為3%，進而依次更佳為2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，P5+ 的含量的下限較佳為0%。另外，P5+ 的含量也可以為0%。In addition, in the optical glass of the present embodiment, the upper limit of the content of P 5+ is preferably 3%, and more preferably 2.5%, 2%, 1.5%, 1%, 0.5%, 0.1%, and 0.05% in this order. Further, the lower limit of the content of P 5+ is preferably 0%. In addition, the content of P 5+ may be 0%.

本實施形態的光學玻璃的陽離子成分較佳主要由上述的成分構成，即較佳由B3+ 、Si4+ 、Al3+ 、La3+ 、Gd3+ 、Y3+ 、Yb3+ 、Zn2+ 、Zr4+ 、Nb5+ 、Ta5+ 、W6+ 、Ti4+ 、Bi3+ 、Li+ 、Na+ 、K+ 、Rb+ 、Cs+ 、Mg2+ 、Ca2+ 、Sr2+ 、Ba2+ 、Ga3+ 、In3+ 、Sc3+ 、Hf4+ 、Lu3+ 、Ge4+ 及P5+ 構成，上述的成分的合計含量較佳大於95%，更佳大於98%，進一步較佳大於99%，再進一步較佳大於99.5%。The cationic component of the optical glass of the present embodiment is preferably mainly composed of the above-mentioned components, that is, B 3+ , Si 4+ , Al 3+ , La 3+ , Gd 3+ , Y 3+ , Yb 3+ , Zn 2+ , Zr 4+ , Nb 5+ , Ta 5+ , W 6+ , Ti 4+ , Bi 3+ , Li + , Na + , K + , Rb + , Cs + , Mg 2+ , Ca 2+ , Sr 2+ , Ba 2+ , Ga 3+ , In 3+ , Sc 3+ , Hf 4+ , Lu 3+ , Ge 4+ and P 5+ , the total content of the above components is preferably greater than 95%, More preferably more than 98%, still more preferably more than 99%, still more preferably more than 99.5%.

在本實施形態的光學玻璃中，Te4+ 的含量的上限較佳為3%，進而依次更佳為2.5%、2%、1.5%、1%、0.5%、0.1%、0.05%。此外，Te4+ 的含量的下限較佳為0%。另外，Te4+ 的含量也可以為0%。In the optical glass of the present embodiment, the upper limit of the content of Te 4+ is preferably 3%, and more preferably 2.5%, 2%, 1.5%, 1%, 0.5%, 0.1%, and 0.05% in this order. Further, the lower limit of the content of Te 4+ is preferably 0%. In addition, the content of Te 4+ may be 0%.

本發明的玻璃為氧化物玻璃，陰離子成分中的主成分為O2- 。陰離子成分O2- 的含量的範圍較佳超過95陰離子%且在100陰離子%以下，更佳超過97陰離子%且在100陰離子%以下，進一步較佳超過99陰離子%且在100陰離子%以下，再進一步較佳超過99.5陰離子%且在100陰離子%以下，更進一步較佳超過99.9陰離子%且在100陰離子%以下，再更進一步較佳為100陰離子%。The glass of the present invention is an oxide glass, and the main component in the anion component is O 2- . The range of the content of the anion component O 2- is preferably more than 95% anion and less than 100% anion, more preferably more than 97% anion and less than 100% anion, more preferably more than 99% anion and less than 100% anion, and then It is more preferably more than 99.5 anion % and below 100 anion %, still more preferably more than 99.9 anion % and less than 100 anion %, still more preferably 100 anion %.

本發明的玻璃也可以包含O2- 以外的陰離子成分。作為O2- 以外的陰離子成分，能夠例示出F- 、Cl- 、Br- 、I- 。但是，F- 、Cl- 、Br- 、I- 均容易在玻璃的熔融過程中揮發。由於這些成分的揮發，會產生玻璃的特性改變、玻璃的均質性下降、熔融設備的消耗變得顯著等問題。因此，F- 、Cl- 、Br- 及I- 的含量的合計較佳不足5陰離子%，更佳不足3陰離子%，進一步較佳不足1陰離子%，再進一步較佳不足0.5陰離子%，更進一步較佳不足0.1陰離子%，再更進一步較佳為0陰離子%。The glass of the present invention may contain anionic components other than O 2- . F - , Cl - , Br - , and I - can be exemplified as anion components other than O 2- . However, F - , Cl - , Br - , and I - all tend to volatilize during the melting process of glass. Due to the volatilization of these components, problems such as a change in the properties of the glass, a decrease in the homogeneity of the glass, and a significant consumption of melting equipment occur. Therefore, the total content of F - , Cl - , Br - and I - is preferably less than 5 anion%, more preferably less than 3 anion%, more preferably less than 1 anion%, still more preferably less than 0.5 anion%, and further Preferably it is less than 0.1 anion %, and still more preferably, it is 0 anion %.

另外，陰離子%是指將全部的陰離子成分的含量的合計設為100%時的莫耳百分率。In addition, anion % means the molar percentage when the sum total of content of all anion components is made into 100%.

本實施形態的光學玻璃較佳基本上由上述成分構成，但是在不妨礙本發明的作用效果的範圍內，也能夠含有其它成分。此外，在本發明中不排除含有不可避免的雜質。The optical glass of the present embodiment is preferably basically composed of the above-mentioned components, but may contain other components within a range that does not inhibit the functions and effects of the present invention. In addition, the inclusion of inevitable impurities is not excluded in the present invention.

第2實施形態中的其它成分組成能夠設為與第1實施形態相同。此外，第2實施形態的玻璃特性、光學玻璃的製造及光學元件等的製造也能夠設為與第1實施形態相同。The other component compositions in the second embodiment can be the same as those in the first embodiment. In addition, the glass properties of the second embodiment, the manufacture of optical glass, the manufacture of optical elements, and the like can also be made the same as those of the first embodiment.

以上對本發明的實施形態進行了說明，但是本發明不限定於這樣的實施形態，可以在不脫離本發明的要點的範圍內以各種方式來實施。As mentioned above, although embodiment of this invention was described, this invention is not limited to such an embodiment, It can implement in various forms in the range which does not deviate from the summary of this invention.

此外，在本說明書中，以質量%表示和陽離子%表示對光學玻璃的玻璃組成進行了說明，但是各表示方法能夠藉由例如後述那樣的換算方法進行相互轉換。In addition, in this specification, although the glass composition of an optical glass was demonstrated in mass % representation and cationic % representation, each representation method can be mutually converted by the conversion method mentioned later, for example.

有時以氧化物為基準來表示玻璃組成的定量分析的結果、玻璃成分，玻璃成分的含量以質量%表示。這樣的組成的表示能夠藉由例如下述的方法換算為以陽離子%、陰離子%表示的組成。The results of the quantitative analysis of the glass composition and the glass components may be expressed on the basis of oxides, and the content of the glass components may be expressed in mass %. The representation of such a composition can be converted into a composition represented by cation % and anion % by, for example, the following method.

由陽離子A和氧構成的氧化物表示為Am On 。m和n分別是根據化學計量法確定的整數。例如，對於B3+ ，以氧化物為基準的表示為B2 O3 ，m=2，n=3，對於Si4+ ，則為SiO2 ，m=1，n=2。 Oxides composed of cations A and oxygen are denoted Am On . m and n are respectively integers determined according to stoichiometry. For example, for B 3+ , the oxide-based representation is B 2 O 3 , m=2, n=3, and for Si 4+ , it is SiO 2 , m=1, n=2.

首先，將以質量%表示的Am On 的含量除以Am On 的分子量，再乘以m。將該值設為P。然後，對所有的玻璃成分求P的總和。當將P的總和設為ΣP時，以使ΣP成為100%的方式對各玻璃成分的P的值進行歸一化的值即為以陽離子%表示的As+ 的含量。在此，s為2n/m。First, divide the content of Am On in mass % by the molecular weight of Am On, and multiply by m . Set this value to P. Then, sum P for all glass components. When the sum of P is assumed to be ΣP, the value obtained by normalizing the value of P of each glass component so that ΣP becomes 100% is the content of As + expressed in cation %. Here, s is 2n/m.

要根據以陽離子%表示的各成分的含量來算出以質量%表示的各成分的含量，只要進行與上述步驟相反的步驟即可。In order to calculate the content of each component represented by mass % from the content of each component represented by cation %, it is sufficient to carry out the steps opposite to the above-mentioned steps.

另外，ΣP中不包含能夠作為澄清劑而少量添加的Sb2 O3 、SnO2 、CeO2 。而且，將Sb2 O3 、SnO2 、CeO2 的各含量設為外加的含量。關於外加的含量，如前所述。In addition, Sb 2 O 3 , SnO 2 , and CeO 2 that can be added in small amounts as a clarifying agent are not included in ΣP. In addition, let each content of Sb2O3 , SnO2 , and CeO2 be an external content. The added content is as described above.

關於上述的分子量，如前所述。The above-mentioned molecular weight is as described above.

[實施例] 以下，藉由實施例對本發明進行更詳細的說明，但是本發明並不限定於這些實施例。[Example] Hereinafter, the present invention will be described in more detail by way of examples, but the present invention is not limited to these examples.

(實施例1) 在表5A～7A和表5B～7B示出本發明的實施例的光學玻璃(試樣1～23)的玻璃組成及其特性值。(Example 1) Tables 5A to 7A and Tables 5B to 7B show the glass compositions and characteristic values of the optical glasses (samples 1 to 23) according to the examples of the present invention.

在此，在表5A～7A中以質量%表示來表示試樣1～23的玻璃組成，在表5B～7B中以陽離子%表示來表示試樣1～23的玻璃組成。即，雖然在表5A～7A和表5B～7B中玻璃組成的表示方法不同，但是相同試樣編號的光學玻璃意味著具有相同組成的相同的光學玻璃。因此，表5A～7A和表5B～7B實質上示出了相同的光學玻璃及其結果。後述的表8A、表8B及表9A、表9B也是同樣的。Here, in Tables 5A to 7A, the glass compositions of Samples 1 to 23 are represented by mass %, and the glass compositions of Samples 1 to 23 are represented by cation % in Tables 5B to 7B. That is, although the representation method of the glass composition is different in Tables 5A to 7A and Tables 5B to 7B, the optical glass of the same sample number means the same optical glass having the same composition. Therefore, Tables 5A to 7A and Tables 5B to 7B show substantially the same optical glass and its results. The same applies to Table 8A, Table 8B, Table 9A, and Table 9B described later.

另外，在表5B～9B中以陽離子%表示來表示玻璃組成，但是陰離子成分均全部為O2- 。即，表5B～9B所述的組成，其O2- 的含量均為100陰離子%。In addition, in Tables 5B to 9B, the glass composition is shown in terms of cation %, but all of the anion components are O 2- . That is, in the compositions described in Tables 5B to 9B, the content of O 2- is all 100% anion.

此外，表5A～9A中的以質量%表示的組成是將表5B～9B中的以陽離子%表示的組成進行變換的組成。In addition, the compositions represented by mass % in Tables 5A to 9A are compositions obtained by converting the compositions represented by cation % in Tables 5B to 9B.

對用以下的步驟製作的光學玻璃進行了各種評價。將結果示於表5A～7A和表5B～7B。Various evaluations were performed about the optical glass produced by the following procedure. The results are shown in Tables 5A to 7A and Tables 5B to 7B.

＜光學玻璃的熔解、成型＞ 準備與玻璃的構成成分對應的氧化物、氫氧化物、碳酸鹽及硝酸鹽作為原材料，以使得到的光學玻璃的玻璃組成為各表所示的各組成的方式稱量、調配上述原材料，將原材料充分混合而製成調配原料。將得到的調配原料(批料原料)放入到鉑坩堝，連同坩堝一起放入到設定為1250～1350℃的範圍的電爐內，一邊進行120～180分鐘的熔融一邊進行攪拌而謀求均質化和脫泡(澄清)。此後，從電爐取出放入有熔融玻璃的鉑坩堝，傾斜鉑坩堝而將熔融玻璃澆鑄到預熱了的模具中。藉由將模具放置在溫度被設定為玻璃化轉變溫度(Tg)附近的電爐中5～10分鐘來進行模具的預熱，在澆鑄熔融玻璃時將模具從電爐中取出進行使用。為了使澆鑄的玻璃的形狀不變形，在將玻璃在鑄模中靜置數秒～數十秒後，將玻璃連同鑄模一起立即轉移到緩冷爐內，在設定為玻璃化轉變溫度Tg附近的緩冷爐內進行大約1小時的退火，然後緩冷至室溫而得到各光學玻璃。另外，試樣的製備全部在大氣環境中進行。<Melting and molding of optical glass> Oxides, hydroxides, carbonates, and nitrates corresponding to the constituent components of the glass were prepared as raw materials, and the above-mentioned raw materials were weighed and prepared so that the glass compositions of the optical glass obtained would be the respective compositions shown in the respective tables. The raw materials are thoroughly mixed to prepare the preparation raw materials. The obtained preparation raw material (batch raw material) was put into a platinum crucible, put into an electric furnace set in the range of 1250 to 1350° C. together with the crucible, and stirred while melting for 120 to 180 minutes to achieve homogenization and Degassed (clarified). After that, the platinum crucible containing the molten glass was taken out from the electric furnace, and the platinum crucible was tilted to cast the molten glass into a preheated mold. The mold is preheated by placing the mold in an electric furnace whose temperature is set near the glass transition temperature (Tg) for 5 to 10 minutes, and the mold is taken out of the electric furnace for use when casting molten glass. In order to prevent the shape of the cast glass from being deformed, after the glass is allowed to stand in the mold for several seconds to several tens of seconds, the glass is immediately transferred to the slow cooling furnace together with the mold, and the slow cooling is set to the vicinity of the glass transition temperature Tg After performing annealing in the furnace for about 1 hour, each optical glass was obtained by slowly cooling to room temperature. In addition, the preparation of the sample was all performed in the atmospheric environment.

在得到的玻璃中未發現原料的熔融殘留、晶體的析出、氣泡等異物，確認為均質性高的光學玻璃。In the obtained glass, foreign matter such as melting residues of raw materials, precipitation of crystals, and bubbles was not found, and it was confirmed that it was an optical glass with high homogeneity.

＜光學玻璃的評價＞ 測定所得到的各光學玻璃的折射率(nd)、阿貝數(νd)、玻璃化轉變溫度(Tg)、著色度(λ80)、著色度(λ5)、比重。<Evaluation of Optical Glass> The refractive index (nd), Abbe number (νd), glass transition temperature (Tg), degree of coloration (λ80), degree of coloration (λ5), and specific gravity of each of the obtained optical glasses were measured.

用如下方法來測定折射率(nd)、阿貝數(νd)、玻璃化轉變溫度(Tg)、比重、著色度(λ5)、著色度(λ80)、液相線溫度。The refractive index (nd), Abbe number (νd), glass transition temperature (Tg), specific gravity, degree of coloration (λ5), degree of coloration (λ80), and liquidus temperature were measured by the following methods.

(1)玻璃組成的確認 選取適量像上述那樣得到的各光學玻璃，使用電感耦合電漿原子發射光譜法(ICP-AES法)對各成分的含量進行定量，由此測定玻璃組成，確認其與表5A～7A和表5B～7B所示的各試樣的氧化物組成一致。(1) Confirmation of glass composition An appropriate amount of each optical glass obtained as described above was selected, and the content of each component was quantified by using inductively coupled plasma atomic emission spectrometry (ICP-AES method) to measure the glass composition and confirm that it is consistent with Tables 5A to 7A and 5B. The oxide compositions of the samples shown in -7B are the same.

(2)折射率(nd)、阿貝數(νd) 根據日本光學玻璃工業會標準的折射率測定法，以可得到能夠充分退火的試樣的形狀(例如40mm×40mm以下的方形，厚度為25mm以下)且足以製作後述的棱鏡的大小的玻璃的方式切斷緩冷至室溫的光學玻璃。然後，以使玻璃的溫度能夠追隨於升溫的升溫速度(例如40～50℃/小時)升溫至玻璃化轉變溫度Tg～(Tg+30℃)之間的溫度，保持90分鐘～180分鐘而除去玻璃中的應力。接著，以降溫速度-30℃/小時×4小時的條件對玻璃進行緩冷，然後藉由放置冷卻而得到光學玻璃。加工得到的光學玻璃而製作棱鏡，使用島津儀器製造公司製造的精密分光計GMR-1(商品名稱)測定折射率(nd)、折射率(nF)、折射率(nc)。此外，使用折射率(nd)、折射率(nF)、折射率(nc)的各測定值算出阿貝數(νd)。(2) Refractive index (nd), Abbe number (νd) According to the refractive index measurement method of the Japan Optical Glass Industry Association, the shape of the sample that can be sufficiently annealed (for example, a square of 40 mm × 40 mm or less, and a thickness of 25 mm or less) and a glass of a size sufficient to produce a prism to be described later can be obtained. Cut the optical glass slowly cooled to room temperature. Then, the temperature of the glass is raised to a temperature between the glass transition temperature Tg and (Tg+30°C) at a temperature increase rate (for example, 40 to 50° C./hour) that allows the temperature of the glass to follow the temperature increase, and the temperature is kept for 90 minutes to 180 minutes and removed. Stress in glass. Next, after slowly cooling the glass on the conditions of a temperature drop rate of −30° C./hour×4 hours, it was left to cool to obtain an optical glass. The obtained optical glass was processed to produce a prism, and the refractive index (nd), refractive index (nF), and refractive index (nc) were measured using a precision spectrometer GMR-1 (trade name) manufactured by Shimadzu Corporation. In addition, the Abbe number (νd) was calculated using each measured value of the refractive index (nd), the refractive index (nF), and the refractive index (nc).

(3)玻璃化轉變溫度(Tg) 使用理學公司(Rigaku Corporation)製造的熱機械分析裝置，以4℃/分鐘的升溫速度進行測定。(3) Glass transition temperature (Tg) The measurement was performed at a temperature increase rate of 4° C./min using a thermomechanical analyzer manufactured by Rigaku Corporation.

(4)比重 藉由阿基米德法進行測定。(4) Specific gravity Measured by the Archimedes method.

(5)著色度(λ5)、著色度(λ80) 將厚度為10mm±0.1mm的玻璃作為試樣，使用分光光度計測定光譜透射率。根據光譜透射率算出λ5、λ80。(5) Coloring degree (λ5), coloring degree (λ80) Spectral transmittance was measured using a spectrophotometer using glass having a thickness of 10 mm±0.1 mm as a sample. λ5 and λ80 were calculated from the spectral transmittance.

(6)液相線溫度 將大約5cc(5ml)玻璃放入到鉑製坩堝中，在1250℃～1350℃加熱15分鐘後，冷卻到玻璃化轉變溫度(Tg)以下。將冷卻了的玻璃移動到規定溫度的爐內保持2小時，然後將未發現晶體的析出的最低溫度定義為液相線溫度。使用倍率為100倍的光學顯微鏡藉由目視方式確定有無晶體析出。(6) Liquidus temperature About 5 cc (5 ml) of glass was put into a platinum crucible, heated at 1250°C to 1350°C for 15 minutes, and then cooled to below the glass transition temperature (Tg). The cooled glass was moved to a furnace at a predetermined temperature and held for 2 hours, and then the minimum temperature at which precipitation of crystals was not observed was defined as the liquidus temperature. The presence or absence of crystal precipitation was visually confirmed using an optical microscope with a magnification of 100 times.

[表5A]

Figure 02_image003
[Table 5A]
Figure 02_image003

[表6A]

Figure 02_image005
[Table 6A]
Figure 02_image005

[表7A]

Figure 02_image007
[Table 7A]
Figure 02_image007

[表5B]

Figure 02_image009
[Table 5B]
Figure 02_image009

[表6B]

Figure 02_image011
[Table 6B]
Figure 02_image011

[表7B]

Figure 02_image013
[Table 7B]
Figure 02_image013

(實施例2) 使用在實施例1中得到的各種光學玻璃製作精密壓製成型用預製件。預製件的製作方法使用公知的方法。(Example 2) Using the various optical glasses obtained in Example 1, preforms for precision press molding were produced. A known method is used for the production method of the preform.

將該預製件在氮環境中加熱、軟化，用壓製成型模進行精密壓製成型而將玻璃成型為非球面透鏡形狀。從壓製成型模取出成型的玻璃進行退火，製作由在實施例1中製作的各種光學玻璃構成的非球面透鏡。The preform was heated and softened in a nitrogen atmosphere, and the glass was molded into an aspheric lens shape by precise press molding with a press molding die. The molded glass was taken out from the press molding die and annealed, and an aspherical lens composed of the various optical glasses produced in Example 1 was produced.

在像這樣製作的非球面透鏡的表面沒有發現白濁(透明性降低)、氣泡、傷痕等缺陷。Defects such as cloudiness (decreased transparency), bubbles, and scratches were not found on the surface of the aspherical lens produced in this manner.

(比較例1) 對專利文獻6(日本特開2009-203083)的實施例1、實施例4、實施例14、實施例19、實施例21這5種組成(試樣24～28)，以可得到具有這些組成的玻璃的方式調配原料，將其放入到鉑製坩堝中，在1300℃經2小時進行熔融。另外，熔融物的質量為200g。(Comparative Example 1) Five compositions (samples 24 to 28) of Example 1, Example 4, Example 14, Example 19, and Example 21 of Patent Document 6 (Japanese Laid-Open Patent Publication No. 2009-203083) can be obtained with these compositions. The raw materials were prepared in the form of glass, put into a platinum crucible, and melted at 1300°C for 2 hours. In addition, the mass of the melt was 200 g.

在表8A和表8B示出試樣24～28的玻璃組成及其特性值。試樣24～28的組成不包含Nb，因此均發生了失透(析出晶體)。The glass compositions of Samples 24 to 28 and their characteristic values are shown in Tables 8A and 8B. Since the compositions of Samples 24 to 28 did not contain Nb, devitrification (precipitation of crystals) occurred in all of them.

[表8A]

Figure 02_image015
[Table 8A]
Figure 02_image015

[表8B]

Figure 02_image017
[Table 8B]
Figure 02_image017

(比較例2) 再現了專利文獻3(日本特開2002-12443)的實施例2、專利文獻7(日本特表2009-537427)的實施例4、實施例8、實施例15的玻璃(試樣29～32)。在表9A和表9B示出試樣29～32的玻璃組成及其特性值。在試樣29～32的組成中，作為揮發性的指標的比RE1/D1、比RE2/D2均小，熔融狀態的玻璃的揮發量增多。(Comparative Example 2) Glasses (samples 29 to 32) that reproduced Example 2 of Patent Document 3 (Japanese Patent Laid-Open No. 2002-12443) and Example 4, Example 8, and Example 15 of Patent Document 7 (Japanese Patent Application Laid-Open No. 2009-537427) . The glass compositions of Samples 29 to 32 and their characteristic values are shown in Tables 9A and 9B. In the compositions of Samples 29 to 32, the ratio RE1/D1 and the ratio RE2/D2, which are indexes of volatility, were both small, and the volatilization amount of the glass in the molten state increased.

[表9A]

Figure 02_image019
[Table 9A]
Figure 02_image019

[表9B]

Figure 02_image021
[Table 9B]
Figure 02_image021

將由試樣29～32的玻璃構成的試樣(大約50mg)在1200℃熔融1小時，測定熔融前後的質量，求出質量減少量和質量減少率。在表10示出試樣29～32的熔融前的質量、由熔融造成的質量減少量和質量減少率。由試樣的熔融造成的質量減少是由於熔融玻璃的揮發而造成的。Samples (about 50 mg) composed of the glasses of Samples 29 to 32 were melted at 1200° C. for 1 hour, the mass before and after melting was measured, and the amount of mass loss and the rate of mass reduction were determined. Table 10 shows the mass before melting, the amount of mass reduction due to melting, and the mass reduction rate of Samples 29 to 32. The mass reduction caused by the melting of the sample is due to the volatilization of the molten glass.

[表10] 試樣編號 熔融前的試樣的質量 質量減少量 質量減少率 試樣29 50.92mg 885.5μg 1.74% 試樣30 48.99mg 986.4μg 2.01% 試樣31 49.48mg 816.8μg 1.65% 試樣32 51.14mg 857.4μg 1.68% [Table 10] Sample No Mass of sample before melting mass reduction mass reduction rate Sample 29 50.92mg 885.5μg 1.74% Sample 30 48.99mg 986.4μg 2.01% Sample 31 49.48mg 816.8μg 1.65% Sample 32 51.14mg 857.4μg 1.68%

另外，試樣的質量減少量根據TG-DTA來測定。另一方面，對本申請實施例的各玻璃進行了同樣的實驗，質量減少率均為0.74%以下，是上述試樣29～32的玻璃的質量減少率的1/3～1/2這樣小的值。In addition, the mass reduction amount of a sample was measured by TG-DTA. On the other hand, the same experiment was carried out for each glass of the examples of the present application, and the mass reduction rate was 0.74% or less, which was as small as 1/3 to 1/2 of the mass reduction rate of the glass of the above-mentioned samples 29 to 32. value.

(比較例3) 將專利文獻7(日本特表2009-537427)的實施例4(試樣30)的玻璃在1200℃分別保持2小時、4小時、6小時，進行冷卻而測定了折射率(nd)，得到表11所示的結果。(Comparative Example 3) The glass of Example 4 (Sample 30) of Patent Document 7 (JP 2009-537427) was kept at 1200° C. for 2 hours, 4 hours, and 6 hours, respectively, and cooled to measure the refractive index (nd), and the table was obtained. 11 shows the results.

[表11] 1200℃保持時間 折射率nd 折射率nd的變化量（註） 2小時 1.79682 0 4小時 1.79923 +0.00241 6小時 1.79991 +0.00309 (註)以在1200℃保持2小時時的折射率(nd)的值為基準。[Table 11] 1200℃ holding time Refractive index nd Amount of change in refractive index nd (Note) 2 hours 1.79682 0 4 hours 1.79923 +0.00241 6 hours 1.79991 +0.00309 (Note) Based on the value of the refractive index (nd) when kept at 1200°C for 2 hours.

另一方面，本申請實施例的試樣16的玻璃的折射率(nd)的變化如表12所示。On the other hand, Table 12 shows the change in the refractive index (nd) of the glass of the sample 16 of the examples of the present application.

[表12] 1200℃保持時間 折射率nd 折射率nd的變化量(註) 2小時 1.82102 0 4小時 1.82138 +0.00036 6小時 1.82157 +0.00055 (註)以在1200℃保持2小時時的折射率(nd)的值為基準。[Table 12] 1200℃ holding time Refractive index nd Variation in refractive index nd (Note) 2 hours 1.82102 0 4 hours 1.82138 +0.00036 6 hours 1.82157 +0.00055 (Note) Based on the value of the refractive index (nd) when kept at 1200°C for 2 hours.

在試樣16以外的本申請實施例的玻璃中，在1200℃保持2小時後的折射率(nd)與保持6小時後的折射率(nd)的差的絕對值也不足0.00070。另外，在任一情況下，與易揮發的成分相比，不易揮發的成分提高折射率的作用強，因此藉由延長保持時間，從而折射率上升。In the glasses of Examples of the present application other than Sample 16, the absolute value of the difference between the refractive index (nd) after holding at 1200° C. for 2 hours and the refractive index (nd) after holding for 6 hours was less than 0.00070. In addition, in any case, since the effect of increasing the refractive index of the less volatile component is stronger than that of the easily volatile component, the refractive index increases by prolonging the holding time.

像這樣，可知藉由增大作為揮發性的指標的比[RE1/D1]、比[RE2/D2]，從而能夠降低揮發，能夠使折射率(nd)的變化量降低到1/7～1/4。As described above, it can be seen that by increasing the ratio [RE1/D1] and the ratio [RE2/D2], which are indicators of volatility, the volatility can be reduced, and the amount of change in the refractive index (nd) can be reduced to 1/7 to 1 /4.

無。none.

圖1是對公知的玻璃將橫軸設為L1相對於NWF1和RE1的合計值的比[L1/(NWF1+RE1)]及將縱軸設為玻璃化轉變溫度(Tg)而繪製的圖。 圖2是對公知的玻璃將橫軸設為L2相對於NWF2和RE2的合計值的比[L2/(NWF2+RE2)]及將縱軸設為玻璃化轉變溫度(Tg)而繪製的圖。1 is a graph plotted with the horizontal axis being the ratio of L1 to the total value of NWF1 and RE1 [L1/(NWF1+RE1)] and the vertical axis being the glass transition temperature (Tg) for a known glass. 2 is a graph plotted with the horizontal axis being the ratio of L2 to the total value of NWF2 and RE2 [L2/(NWF2+RE2)] and the vertical axis being the glass transition temperature (Tg) for a known glass.

Claims (4)

一種光學玻璃，在該光學玻璃中，RE1相對於NWF1的比[RE1/NWF1]為0.35以上； HR1相對於RE1的比[HR1/RE1]為0.33以下； Nb2 O5 的含量相對於Nb2 O5 和Ta2 O5 的合計含量的質量比[Nb2 O5 /(Nb2 O5 +Ta2 O5 )]為2/3以上； RE1相對於D1的比[RE1/D1]為0.90以上； L1相對於NWF1和RE1的合計值的比[L1/(NWF1+RE1)]為0.78以上； D1為0.16以上； 阿貝數(νd)為39.0以上、未滿45.0，該阿貝數(νd)與折射率(nd)滿足下述式(1)： 式(1) nd≥2.235-0.01×νd 式中： 當將M(B2 O3 )、M(SiO2 )、M(Al2 O3 )、M(La2 O3 )、M(Gd2 O3 )、M(Y2 O3 )、M(Yb2 O3 )、M(LaF3 )、M(GdF3 )、M(YF3 )、M(YbF3 )、M(ZnO)、M(Li2 O)、M(Na2 O)、M(K2 O)、M(ZrO2 )、M(Nb2 O5 )、M(TiO2 )、M(WO3 )、M(Ta2 O5 )、M(Bi2 O3 )、M(MgO)、M(CaO)、M(SrO)、M(BaO)分別設為B2 O3 、SiO2 、Al2 O3 、La2 O3 、Gd2 O3 、Y2 O3 、Yb2 O3 、LaF3 、GdF3 、YF3 、YbF3 、ZnO、Li2 O、Na2 O、K2 O、ZrO2 、Nb2 O5 、TiO2 、WO3 、Ta2 O5 、Bi2 O3 、MgO、CaO、SrO、BaO的分子量時； NWF1=[2×B2 O3 /M(B2 O3 )]+[SiO2 /M(SiO2 )]+[2×Al2 O3 /M(Al2 O3 )]； RE1=[2×La2 O3 /M(La2 O3 )]+[2×Gd2 O3 /M(Gd2 O3 )]+[2×Y2 O3 /M(Y2 O3 )]+[2×Yb2 O3 /M(Yb2 O3 )]+[LaF3 /M(LaF3 )]+[GdF3 /M(GdF3 )]+[YF3 /M(YF3 )]+[YbF3 /M(YbF3 )]； HR1=[2×Nb2 O5 /M(Nb2 O5 )]+[TiO2 /M(TiO2 )]+[WO3 /M(WO3 )]+[2×Bi2 O3 /M(Bi2 O3 )]； D1={[2×Li2 O/M(Li2 O)]+[2×Na2 O/M(Na2 O)]+[2×K2 O/M(K2 O)]}×3+[ZnO/M(ZnO)]； L1=[20×Li2 O/M(Li2 O)]+[16×Na2 O/M(Na2 O)]+[8×K2 O/M(K2 O)]+[4×ZnO/M(ZnO)]+[MgO/M(MgO)]+[2×CaO/M(CaO)]+[2×SrO/M(SrO)]+[2×BaO/M(BaO)]+[2×B2 O3 /M(B2 O3 )]+[2×Nb2 O5 /M(Nb2 O5 )]+[TiO2 /M(TiO2 )]+[4×WO3 /M(WO3 )]+[8×Bi2 O3 /M(Bi2 O3 )]+[2×Ta2 O5 /M(Ta2 O5 )]-[2×SiO2 /M(SiO2 )]-[2×Al2 O3 /M(Al2 O3 )]-[2×ZrO2 /M(ZrO2 )]-[2×La2 O3 /M(La2 O3 )]-[2×Gd2 O3 /M(Gd2 O3 )]-[2×Y2 O3 /M(Y2 O3 )]-[2×Yb2 O3 /M(Yb2 O3 )]-[LaF3 /M(LaF3 )]-[GdF3 /M(GdF3 )]-[YF3 /M(YF3 )]-[YbF3 /M(YbF3 )]； 上述各玻璃成分的含量為以質量%表示的值。An optical glass, in which the ratio of RE1 to NWF1 [RE1/NWF1] is 0.35 or more; the ratio of HR1 to RE1 [HR1/RE1] is 0.33 or less; the content of Nb 2 O 5 relative to Nb 2 The mass ratio of the total content of O 5 and Ta 2 O 5 [Nb 2 O 5 /(Nb 2 O 5 +Ta 2 O 5 )] is 2/3 or more; the ratio of RE1 to D1 [RE1/D1] is 0.90 or more; the ratio of L1 to the total value of NWF1 and RE1 [L1/(NWF1+RE1)] is 0.78 or more; D1 is 0.16 or more; Abbe number (νd) is 39.0 or more and less than 45.0, the Abbe number ( νd) and refractive index (nd) satisfy the following formula (1): Formula (1) nd≥2.235-0.01×νd In the formula: When M(B 2 O 3 ), M(SiO 2 ), M(Al 2 O 3 ), M(La 2 O 3 ), M(Gd 2 O 3 ), M(Y 2 O 3 ), M(Yb 2 O 3 ), M(LaF 3 ), M(GdF 3 ), M( YF 3 ), M(YbF 3 ), M(ZnO), M(Li 2 O), M(Na 2 O), M(K 2 O), M(ZrO 2 ), M(Nb 2 O 5 ), M(TiO 2 ), M(WO 3 ), M(Ta 2 O 5 ), M(Bi 2 O 3 ), M(MgO), M(CaO), M(SrO), and M(BaO) are respectively set as B 2 O 3 , SiO 2 , Al 2 O 3 , La 2 O 3 , Gd 2 O 3 , Y 2 O 3 , Yb 2 O 3 , LaF 3 , GdF 3 , YF 3 , YbF 3 , ZnO, Li 2 O , Na 2 O, K 2 O, ZrO 2 , Nb 2 O 5 , TiO 2 , WO 3 , Ta 2 O 5 , Bi 2 O 3 , MgO, CaO, SrO, BaO molecular weight; NWF1=[2×B 2 O 3 /M(B 2 O 3 )]+[SiO 2 /M(SiO 2 )]+[2×Al 2 O 3 /M(Al 2 O 3 )]; RE1=[2×La 2 O 3 /M(La 2 O 3 )]+[2×Gd 2 O 3 /M(Gd 2 O 3 )]+[2×Y 2 O 3 /M(Y 2 O 3 )]+[2×Yb 2 O 3 /M(Yb 2 O 3 )]+[LaF 3 /M(LaF 3 )]+[GdF 3 /M(GdF 3 )]+[YF 3 /M(YF 3 )]+[YbF 3 /M(YbF 3 )]; HR1=[2×Nb 2 O 5 /M(Nb 2 O 5 )]+[TiO 2 /M(TiO 2 )]+[WO 3 /M( WO 3 )]+[2×Bi 2 O 3 /M(Bi 2 O 3 )]; D1={[2×Li 2 O/M(Li 2 O)]+[2×Na 2 O/M(Na 2 O)]+[2×K 2 O/M(K 2 O)]}×3+[ZnO/M(ZnO)]; L1=[20×Li 2 O/M(Li 2 O)]+[ 16×Na 2 O/M(Na 2 O)]+[8×K 2 O/M(K 2 O)]+[4×ZnO/M(ZnO)]+[MgO/M(MgO)]+[ 2×CaO/M(CaO)]+[2×SrO/M(SrO)]+[2×BaO/M(BaO)]+[2×B 2 O 3 /M(B 2 O 3 )]+[ 2×Nb 2 O 5 /M(Nb 2 O 5 )]+[TiO 2 /M(TiO 2 )]+[4×WO 3 /M(WO 3 )]+[8×Bi 2 O 3 /M( Bi 2 O 3 )]+[2×Ta 2 O 5 /M(Ta 2 O 5 )]-[2×SiO 2 /M(SiO 2 )]-[2×Al 2 O 3 /M(Al 2 O 3 )]-[2×ZrO 2 /M(ZrO 2 )]-[2×La 2 O 3 /M(La 2 O 3 )]-[2×Gd 2 O 3 /M(Gd 2 O 3 )] -[2×Y 2 O 3 /M(Y 2 O 3 )]-[2×Yb 2 O 3 /M(Yb 2 O 3 )]-[LaF 3 /M(LaF 3 )]-[GdF 3 / M(GdF 3 )]-[YF 3 /M(YF 3 )]-[YbF 3 /M(YbF 3 )]; The content of each of the above glass components is a value represented by mass %. 一種光學玻璃，該光學玻璃是氧化物玻璃，在該光學玻璃中，RE2相對於NWF2的比[RE2/NWF2]為0.35以上； HR2相對於RE2的比[HR2/RE2]為0.33以下； Nb5+ 的含量相對於Nb5+ 和Ta5+ 的合計含量的陽離子比[Nb5+ /(Nb5+ +Ta5+ )]為3/4以上； RE2相對於D2的比[RE2/D2]為0.90以上； L2相對於NWF2和RE2的合計值的比[L2/(NWF2+RE2)]為0.78以上； D2為12.44以上； 阿貝數(νd)為39.0以上、未滿45.0，該阿貝數(νd)與折射率(nd)滿足下述式(1)： 式(1) nd≥2.235-0.01×νd 式中： NWF2為B3+ 、Si4+ 及Al3+ 的合計含量； RE2為La3+ 、Gd3+ 、Y3+ 及Yb3+ 的合計含量； HR2為Nb5+ 、Ti4+ 、W6+ 及Bi3+ 的合計含量； D2=(Li+ +Na+ +K+ )×6+Zn2+ ； L2=(10×Li+ )+(8×Na+ )+(4×K+ )+(4×Zn+ )+Mg2+ +(2×Ca2+ )+(2×Sr2+ )+(2×Ba2+ )+B3+ +Nb5+ +Ti4+ +(4×W6+ )+(4×Bi3+ )+Ta5+ -(2×Si4+ )-Al3+ -(2×Zr4+ )-La3+ -Gd3+ -Y3+ -Yb3+ ； 上述各玻璃成分的含量為以陽離子%表示的值。An optical glass, which is an oxide glass, in which the ratio of RE2 to NWF2 [RE2/NWF2] is 0.35 or more; the ratio of HR2 to RE2 [HR2/RE2] is 0.33 or less; Nb 5 The cation ratio of the + content to the total content of Nb 5+ and Ta 5+ [Nb 5+ /(Nb 5+ +Ta 5+ )] is 3/4 or more; the ratio of RE2 to D2 [RE2/D2] is 0.90 or more; the ratio of L2 to the total value of NWF2 and RE2 [L2/(NWF2+RE2)] is 0.78 or more; D2 is 12.44 or more; Abbe number (νd) is 39.0 or more and less than 45.0, the Abbe The number (νd) and the refractive index (nd) satisfy the following formula (1): Formula (1) nd≥2.235-0.01×νd where: NWF2 is the total content of B 3+ , Si 4+ and Al 3+ ; RE2 is the total content of La 3+ , Gd 3+ , Y 3+ and Yb 3+ ; HR2 is the total content of Nb 5+ , Ti 4+ , W 6+ and Bi 3+ ; D2=(Li + +Na + + K + )×6+Zn 2+ ; L2=(10×Li + )+(8×Na + )+(4×K + )+(4×Zn + )+Mg 2+ +(2×Ca 2+ )+(2×Sr 2+ )+(2×Ba 2+ )+B 3+ +Nb 5+ +Ti 4+ +(4×W 6+ )+(4×Bi 3+ )+Ta 5+ - (2×Si 4+ )-Al 3+ -(2×Zr 4+ )-La 3+ -Gd 3+ -Y 3+ -Yb 3+ ; The content of each of the above-mentioned glass components is a value represented by cation %. 一種精密壓製成型用預製件，由如請求項1或2所述之光學玻璃構成。A preform for precision press molding, consisting of the optical glass described in claim 1 or 2. 一種光學元件，由如請求項1或2所述之光學玻璃構成。An optical element composed of the optical glass as described in claim 1 or 2.
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