TWI743061B - Optical glass, preforms and optical components - Google Patents

Optical glass, preforms and optical components Download PDF

Info

Publication number
TWI743061B
TWI743061B TW105136050A TW105136050A TWI743061B TW I743061 B TWI743061 B TW I743061B TW 105136050 A TW105136050 A TW 105136050A TW 105136050 A TW105136050 A TW 105136050A TW I743061 B TWI743061 B TW I743061B
Authority
TW
Taiwan
Prior art keywords
less
component
glass
still
optical
Prior art date
Application number
TW105136050A
Other languages
Chinese (zh)
Other versions
TW201731785A (en
Inventor
桃野浄行
Original Assignee
日商小原股份有限公司
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from JP2016137865A external-priority patent/JP6808385B2/en
Priority claimed from JP2016210891A external-priority patent/JP6903373B2/en
Priority claimed from JP2016210892A external-priority patent/JP6866012B2/en
Application filed by 日商小原股份有限公司 filed Critical 日商小原股份有限公司
Publication of TW201731785A publication Critical patent/TW201731785A/en
Application granted granted Critical
Publication of TWI743061B publication Critical patent/TWI743061B/en

Links

Classifications

    • 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

Landscapes

  • Chemical & Material Sciences (AREA)
  • Life Sciences & Earth Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • General Chemical & Material Sciences (AREA)
  • Geochemistry & Mineralogy (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Glass Compositions (AREA)

Abstract

本發明之目的在於更便宜地取得折射率(nd )及阿貝數(νd )在期望範圍內，且耐失透性高之玻璃。 本發明之光學玻璃以莫耳%計，含有B2 O3 成分5.0%以上55.0%以下，La2 O3 成分5.0%以上30.0%以下，莫耳和(Nb2 O5 +WO3 )未達10.0%，具有1.70以上之折射率(nd )，且具有25以上50以下之阿貝數(νd )。該光學玻璃可用於各種光學元件及光學設計。The object of the present invention is to obtain a glass with a refractive index (n d ) and Abbe number (ν d ) within a desired range and high devitrification resistance at a lower cost. The optical glass of the present invention contains B 2 O 3 component 5.0% or more and 55.0% or less, La 2 O 3 component 5.0% or more and 30.0% or less in molar %, and the molar sum (Nb 2 O 5 +WO 3 ) is not up to 10.0%, with a refractive index (n d ) above 1.70, and an Abbe number (ν d ) above 25 and below 50. The optical glass can be used for various optical elements and optical designs.

Description

光學玻璃、預成形材及光學元件Optical glass, preforms and optical components

本發明係關於一種光學玻璃、預成形材及光學元件。The invention relates to an optical glass, a preformed material and an optical element.

近年來，使用光學系統之機器之數位化或高精細化正快速發展，於數位相機或攝像機等之攝影機器、投影機或投影電視等圖像播放(投影)機器等之各種光學機器之領域中，對於削減光學系統所用之透鏡或稜鏡等之光學元件之片數，使光學系統整體輕量化及小型化之要求不斷增強。 於製作光學元件之光學玻璃中，亦尤其對可謀求光學系統整體之輕量化及小型化之具有1.70以上之折射率(nd )，且阿貝數(νd )為25以上50以下之高折射率低分散玻璃有非常高的需求。作為此種高折射率低分散玻璃，已知有如專利文獻1～8所代表之玻璃組成物。 [先前技術文獻] [專利文獻] [專利文獻1]日本專利特開2011-178571號公報 [專利文獻2]日本專利特開2014-047099號公報 [專利文獻3]日本專利特開2013-067558號公報 [專利文獻4]日本專利特開2012-214350號公報 [專利文獻5]日本專利特開2011-093781號公報 [專利文獻6]日本專利特開2009-203155號公報 [專利文獻7]日本專利特開2011-173783號公報 [專利文獻8]日本專利特開2011-225383號公報In recent years, the digitization or high-definition of equipment using optical systems is rapidly developing, in the field of various optical equipment such as digital cameras or video cameras, and image playback (projection) equipment such as projectors or projection televisions. , For the reduction of the number of optical elements such as lenses or ridges used in the optical system, the requirements for the overall lightweight and miniaturization of the optical system are continuously increasing. In the optical glass used for the production of optical elements, it is especially useful for lightening and miniaturization of the entire optical system, which has a refractive index (n d ) of 1.70 or more, and an Abbe number (ν d ) of 25 to 50. There is a very high demand for low refractive index dispersion glass. As such high-refractive-index low-dispersion glass, the glass composition represented by patent documents 1-8 is known. [Prior Art Document] [Patent Document] [Patent Document 1] Japanese Patent Laid-Open No. 2011-178571 [Patent Document 2] Japanese Patent Laid-Open No. 2014-047099 [Patent Document 3] Japanese Patent Laid-Open No. 2013-067558 Publication [Patent Document 4] Japanese Patent Laid-Open No. 2012-214350 [Patent Document 5] Japanese Patent Laid-Open No. 2011-093781 [Patent Document 6] Japanese Patent Laid-Open No. 2009-203155 [Patent Document 7] Japanese Patent Japanese Patent Application Publication No. 2011-173783 [Patent Document 8] Japanese Patent Application Publication No. 2011-225383

[發明所欲解決之問題] 作為由光學玻璃製作光學元件之方法，例如，已知有對由光學玻璃形成之玻璃坯或玻璃塊進行研削及研磨而獲得光學元件形狀之方法、對將由光學玻璃形成之玻璃坯或玻璃塊再加熱而成形(再熱壓製成形)所得之玻璃成形體進行研削及研磨之方法、及以由玻璃坯或玻璃塊取得之預成形材經超精密加工後之模具加以成形(精密模具壓製成形)而獲得光學元件之形狀的方法。任一方法均要求在由熔融之玻璃原料形成玻璃坯或玻璃塊時，獲得穩定之玻璃。此處，構成所得之玻璃坯或玻璃塊之玻璃對失透之穩定性(耐失透性)下降且於玻璃內部產生結晶之情形，已無法獲得適於作為光學元件之玻璃。 又，為了降低光學玻璃之材料成本，構成光學玻璃之諸多成分之原料費期望儘可能便宜。又，量產光學玻璃時，期望不易引起玻璃製作時之失透。然而，專利文獻1～8所記述之玻璃組成物尚難謂係充分滿足該等諸多要求者。 本發明係鑑於上述問題點而完成者，其目的在於更便宜地獲得折射率(nd )及阿貝數(νd )在期望範圍內，且耐失透性較高之玻璃。 [解決問題之技術手段] 本發明人等為了解決上述問題而反復積極試驗研究，結果發現於含有B2 O3 成分及La2 O3 成分之玻璃中，折射率(nd )及阿貝數(νd )在期望範圍內，且材料成本較高之成分，尤其Nb2 O5 成分或WO3 成分之含有量降低，且玻璃之液相溫度變低，從而完成本發明。 具體而言，本發明提供如下所述者。 (1) 一種光學玻璃，其以莫耳%計，含有 B2 O3 成分5.0%以上55.0%以下， La2 O3 成分5.0%以上30.0%以下，且 莫耳和(Nb2 O5 +WO3 )未達10.0%， 具有1.70以上之折射率(nd )，且具有25以上50以下之阿貝數(νd )。 (2) 如(1)之光學玻璃，其具有1.75以上之折射率(nd )，且具有25以上48以下之阿貝數(νd )。 (3) 如(1)或(2)之光學玻璃，其具有1.70以上1.90以下之折射率(nd )，且具有30以上50以下之阿貝數(νd )。 (4) 如(1)至(3)中任一項之光學玻璃，其中以莫耳%計，含有合計0%以上30.0%以下之CaO成分及BaO成分中至少一者。 (5) 如(1)至(4)中任一項之光學玻璃，其中以莫耳%計， SiO2 成分為0～25.0% ZnO成分為0～45.0% ZrO2 成分為0～15.0%。 (6) 如(1)至(5)中任一項之光學玻璃，其以按莫耳%計， Nb2 O5 成分為0～未達10.0% WO3 成分為0～未達10.0% Gd2 O3 成分為0～未達4.0% Yb2 O3 成分為0～未達4.0% Ta2 O5 成分為0～未達5.0% TiO2 成分為0～未達40.0% Y2 O3 成分為0～25.0% MgO成分為0～10.0% CaO成分為0～10.0% SrO成分為0～10.0% BaO成分為0～25.0% Li2 O成分為0～10.0% Na2 O成分為0～10.0% K2 O成分為0～10.0% P2 O5 成分為0～10.0% GeO2 成分為0～10.0% Al2 O3 成分為0～15.0% Ga2 O3 成分為0～15.0% Bi2 O3 成分為0～15.0% TeO2 成分為0～15.0% SnO2 成分為0～3.0% Sb2 O3 成分為0～1.0%， 作為與上述各金屬元素之1種或2種以上之氧化物之一部分或全部置換之氟化物之F之含有量為0～15.0莫耳%。 (7) 如(1)至(6)中任一項之光學玻璃，其中莫耳比SiO2 /B2 O3 為0.13以上1.70以下。 (8) 如(1)至(7)中任一項之光學玻璃，其中莫耳和Ta2 O5 +Nb2 O5 +WO3 +Gd2 O3 +Yb2 O3 未達10.0%。 (9) 如(1)至(8)中任一項之光學玻璃，其中莫耳比ZnO/(La2 O3 +Y2 O3 )為0.10以上4.00以下。 (10) 如(1)至(9)中任一項之光學玻璃，其中Ln2 O3 成分(式中，Ln係選自由La、Gd、Y、Yb、Lu所組成之群中之1種以上)之莫耳和為5.0%以上40.0%以下， RO成分(式中，R係選自由Mg、Ca、Sr、Ba所組成之群中之1種以上)之莫耳和為25.0%以下， Rn2 O成分(式中，Rn係選自由Li、Na、K所組成之群中之1種以上)之莫耳和為10.0%以下。 (11) 如(1)至(10)中任一項之光學玻璃，其中莫耳比(RO+ZnO)/Ln2 O3 超過0.30(式中，R係選自由Mg、Ca、Sr、Ba所組成之群中之1種以上，Ln係選自由La、Gd、Y、Yb、Lu所組成之群中之1種以上)。 (12) 一種預成形材，其包含如(1)至(11)中任一項之光學玻璃。 (13) 一種光學元件，其包含如(1)至(11)中任一項之光學玻璃。 (14) 一種光學機器，其包含如(12)或(13)之光學元件。 [發明之效果] 根據本發明，可更便宜獲得折射率(nd )及阿貝數(νd )在期望範圍內，且耐失透性較高之玻璃。[Problem to be Solved by the Invention] As a method of manufacturing optical elements from optical glass, for example, there are known methods of grinding and grinding a glass blank or glass block formed of optical glass to obtain the shape of an optical element. The formed glass blank or glass block is reheated to form (re-hot press forming) the resulting glass formed body is ground and ground, and the preform obtained from the glass blank or glass block is ultra-precisely processed into a mold A method of forming (precision mold press forming) to obtain the shape of an optical element. Either method requires obtaining stable glass when forming glass blanks or glass blocks from molten glass raw materials. Here, when the stability of the glass constituting the obtained glass blank or glass block against devitrification (devitrification resistance) is reduced and crystals are generated inside the glass, it is no longer possible to obtain glass suitable as an optical element. In addition, in order to reduce the material cost of optical glass, it is desirable that the raw material cost of many components constituting the optical glass be as cheap as possible. In addition, when mass-produced optical glass, it is desirable to prevent devitrification during glass production. However, the glass compositions described in Patent Documents 1 to 8 cannot be said to sufficiently satisfy these many requirements. The present invention was made in view of the above-mentioned problems, and its object is to obtain a glass having a refractive index (n d ) and Abbe number (ν d ) within a desired range and having high devitrification resistance at a lower cost. [Technical Means to Solve the Problem] In order to solve the above-mentioned problems, the inventors of the present invention conducted repeated experiments and studies, and found that the refractive index (n d ) and Abbe number of glass containing B 2 O 3 and La 2 O 3 (ν d ) is within the desired range, and the material cost is relatively high, especially the content of Nb 2 O 5 component or WO 3 component is reduced, and the liquid phase temperature of the glass is lowered, thus completing the present invention. Specifically, the present invention provides those described below. (1) An optical glass containing 5.0% to 55.0% of B 2 O 3 component, 5.0% to 30.0% of La 2 O 3 component, and molar and (Nb 2 O 5 +WO 3 ) Less than 10.0%, with refractive index (n d ) above 1.70, and Abbe number (ν d ) above 25 and below 50. (2) The optical glass as in (1), which has a refractive index (n d ) of 1.75 or more, and an Abbe number (ν d ) of 25 or more and 48 or less. (3) The optical glass of (1) or (2), which has a refractive index (n d ) of 1.70 or more and 1.90 or less, and an Abbe number (ν d ) of 30 or more and 50 or less. (4) The optical glass according to any one of (1) to (3), which contains at least one of a total of 0% or more and 30.0% or less of CaO component and BaO component in molar %. (5) The optical glass according to any one of (1) to (4), wherein the SiO 2 component is 0-25.0%, the ZnO component is 0-45.0%, and the ZrO 2 component is 0-15.0% in terms of mole%. (6) For the optical glass of any one of (1) to (5), the Nb 2 O 5 component is 0 to less than 10.0% in molar %, and the WO 3 component is 0 to less than 10.0% Gd 2 O 3 content is 0 to less than 4.0% Yb 2 O 3 content is 0 to less than 4.0% Ta 2 O 5 content is 0 to less than 5.0% TiO 2 content is 0 to less than 40.0% Y 2 O 3 content 0～25.0% MgO component 0～10.0% CaO component 0～10.0% SrO component 0～10.0% BaO component 0～25.0% Li 2 O component 0～10.0% Na 2 O component 0～10.0 % K 2 O component is 0～10.0% P 2 O 5 component is 0～10.0% GeO 2 component is 0～10.0% Al 2 O 3 component is 0～15.0% Ga 2 O 3 component is 0～15.0% Bi 2 O 3 component is 0 to 15.0% TeO 2 component is 0 to 15.0% SnO 2 component is 0 to 3.0% Sb 2 O 3 component is 0 to 1.0%, as an oxidation of one or more of the above metal elements The content of F in the fluoride that is partially or completely replaced by one of the substances is 0 to 15.0 mol%. (7) The optical glass of any one of (1) to (6), wherein the molar ratio SiO 2 /B 2 O 3 is 0.13 or more and 1.70 or less. (8) The optical glass as in any one of (1) to (7), wherein the molar ratio of Ta 2 O 5 + Nb 2 O 5 + WO 3 + Gd 2 O 3 + Yb 2 O 3 is less than 10.0%. (9) The optical glass of any one of (1) to (8), wherein the molar ratio ZnO/(La 2 O 3 +Y 2 O 3 ) is 0.10 or more and 4.00 or less. (10) The optical glass of any one of (1) to (9), wherein the Ln 2 O 3 component (where Ln is selected from the group consisting of La, Gd, Y, Yb, and Lu) The molar sum of the above) is 5.0% or more and 40.0% or less, and the RO component (where R is selected from the group consisting of Mg, Ca, Sr, and Ba) has a molar sum of 25.0% or less, The molar sum of the Rn 2 O component (in the formula, Rn is one or more selected from the group consisting of Li, Na, and K) is 10.0% or less. (11) The optical glass of any one of (1) to (10), wherein the molar ratio (RO+ZnO)/Ln 2 O 3 exceeds 0.30 (where R is selected from Mg, Ca, Sr, Ba One or more types in the group formed, Ln is one or more types selected from the group consisting of La, Gd, Y, Yb, and Lu). (12) A preformed material comprising the optical glass as described in any one of (1) to (11). (13) An optical element comprising the optical glass of any one of (1) to (11). (14) An optical machine, which contains an optical element such as (12) or (13). [Effects of the Invention] According to the present invention, it is possible to obtain a glass with a refractive index (n d ) and Abbe number (ν d ) within a desired range at a lower cost and with high devitrification resistance.

本發明之光學玻璃以莫耳%計，含有5.0%以上55.0%以下之B2 O3 成分，及5.0%以上30.0%以下之La2 O3 成分，且莫耳和(Nb2 O5 +WO3 )未達10.0%，具有1.70以上之折射率(nd )，並具有25以上50以下之阿貝數(νd )。 藉由以B2 03 成分及La2 O3 成分為基礎，容易獲得尤其具有1.70以上之折射率(nd )及25以上50以下之阿貝數(νd )，且穩定之玻璃。又，本申請案發明人發現，於尤其具有1.70以上之折射率(nd )及25以上50以下之阿貝數(νd )之玻璃中，使材料成本較高之成分，尤其Nb2 O5 成分或WO3 成分之含量減低之情形，玻璃之液相溫度亦變低，尤其可於玻璃製作時降低失透。因此，可更便宜獲得折射率(nd )及阿貝數(νd )在期望範圍內，且耐失透性較高之光學玻璃。 此外，本發明之光學玻璃由於關於可見光之透射率高故可較佳地用於透射可見光之用途。 其中，亦可將具有1.75以上之折射率(nd )，且25以上48以下之阿貝數(νd )者作為第1光學玻璃。又，亦可將具有1.70以上1.90以下之折射率(nd )，且30以上50以下之阿貝數(νd )者作為第2光學玻璃。 又，亦可將含有CaO成分及BaO成分中至少一者合計超過0%且30.0%以下者作為第3光學玻璃。藉由含有CaO成分及BaO成分中至少一者，容易獲得具有1.70以上之折射率(nd )及25以上50以下之阿貝數(νd )，且更穩定之玻璃。又，尤其藉由含有CaO成分及BaO成分中至少一者，而獲得期望之高折射率且提高可見光之短波長側之光之透射率。又，除Nb2 O5 成分或WO3 成分外，藉由減少稀土類之合計量，亦可謀求進一步成本降低。 以下，詳細地說明本發明之光學玻璃之實施形態。本發明並非對以下實施形態進行任何限定者，在本發明之目的範圍內，可加入適當變更而實施。另，雖存在對於重複說明之處省略適當說明之情形，但並非限定發明之主旨。 [玻璃成分] 以下描述構成本發明之光學玻璃之各成分之組成範圍。於本說明書中，各成分之含量於無特別說明之情形，係以相對於全部氧化物換算組成之總莫耳數的莫耳%表示者。此處，「氧化物換算組成」係於假設作為本發明之玻璃構成成分之原料而使用之氧化物、複合鹽、金屬氟化物等熔融時全部分解且轉化成氧化物之情形，將該生成氧化物之總莫耳數設為100莫耳%，記述玻璃含有之各成分之組成。 ＜關於必須成分、任意成分＞ B2 O3 成分於包含較多稀土類氧化物之本發明之光學玻璃中，係作為玻璃形成氧化物之必須成分。尤其，藉由將B2 O3 成分之含量設為5.0%以上，而提高玻璃之耐失透性，且提高玻璃之阿貝數。因此，B2 O3 成分之含量較佳為5.0%以上，更佳為10.0%以上，進而更佳為超過10.0%，進而更佳為超過14.0%，進而更佳為15.0%以上，進而更佳為超過15.0%，進而更佳為超過19.0%，進而更佳為20.0%以上，進而更佳為超過20.0%，進而更佳在25.0%以上。 另一方面，藉由將B2 O3 成分之含量設為55.0%以下，可容易獲得更大之折射率，且抑制化學耐久性之惡化。因此，B2 O3 成分之含量較佳為55.0%以下，更佳為未達51.0%，進而更佳為50.0%以下，進而更佳為未達47.0%，進而更佳為未達45.0%，進而更佳為未達42.0%，進而更佳為未達40.0%，進而更佳為未達38.0%。 B2 O3 成分係可使用H3 BO3 、Na2 B4 O7 、Na2 B4 O7 ・10H2 O、BPO4 等作為原料。 La2 O3 成分係提高玻璃折射率及阿貝數之必須成分。因此，La2 O3 成分之含量較佳為5.0%以上，更佳為超過7.0%，進而更佳為超過8.0%，進而更佳為超過10.0%。 另一方面，藉由將La2 O3 成分之含量設為30.0%以下，可藉由提高玻璃之穩定性而降低失透，且抑制阿貝數之過度上升。又，提高玻璃原料之熔解性。因此，La2 O3 成分之含量較佳為30.0%以下，更佳為未達25.0%，進而更佳為未達22.0%，進而更佳為未達21.0%，進而更佳為未達20.0%，進而更佳為19.5%以下，進而更佳為17.5%以下，進而更佳為16.5%以下，進而更佳為14.5%以下。 La2 O3 成分可使用La2 O3 、La(NO3 )3 ・XH2 O(X為任意之整數)等作為原料。 Nb2 O5 成分及WO3 成分之合計量較佳設為未達10.0%。藉此，因該等昂貴成分之含量被降低，故可抑制玻璃之材料成本。因此，莫耳和(Nb2 O5 +WO3 )較佳為未達10.0%，更佳為未達5.0%，進而更佳為未達3.0%，進而更佳為未達2.0%，進而更佳為未達1.5%，進而更佳為未達1.0%，進而更佳為未達0.5%，進而更佳為未達0.1%。 CaO成分及BaO成分之至少一者較佳合計含有超過0%且30.0%以下。 尤其，藉由將其和設為超過0%，而提高玻璃之折射率或可見光透射率。又，因藉此減少稀土類之含量，故亦可謀求進一步降低成本。因此，莫耳和(CaO+BaO)較佳為超過0%，更佳為超過1.0%，進而更佳為超過2.0%。 另一方面，藉由將其和設為30.0%以下，因玻璃之液相溫度變低，故可降低玻璃之失透。因此，莫耳和(CaO+BaO)較佳為30.0%以下，更佳為未達25.0%，進而更佳為未達20.0%，進而更佳為未達15.0%。 SiO2 成分於含有超過0%之情形，係可提高熔融玻璃之黏度且減低玻璃著色之任意成分。又，亦係容易獲得玻璃之穩定性提高且耐於量產之玻璃的成分。因此，SiO2 成分之含量亦較佳為超過0%，更佳為超過1.0%，進而更佳為超過5.0%，進而更佳為超過8.0%，進而更佳為超過10.2%，進而更佳為超過10.5%。 另一方面，藉由將SiO2 成分之含量設為25.0%以下，而抑制玻璃轉移點之上升，且抑制折射率之下降。因此，SiO2 成分之含量較佳為25.0%，更佳為未達22.0%，進而更佳為未達20.0%，進而更佳為未達18.0%，進而更佳為未達15.5%，進而更佳為未達14.0%。 SiO2 成分可使用SiO2 、K2 SiF6 、Na2 SiF6 等作為原料。 ZnO成分於含有超過0%之情形，係提高原料之熔解性，促進自熔解之玻璃之脫泡，且，提高玻璃之穩定性之任意成分。又，亦係藉由可縮短熔解時間等，而可降低玻璃著色之成分。又，亦係可降低玻璃轉移點，且可改善化學耐久性之成分。因此，ZnO成分之含量亦較佳為超過0%，更佳為超過1.0%，進而更佳為超過2.2%，進而更佳為超過2.5%，進而更佳為超過4.2%，進而更佳為超過4.5%，進而更佳為超過5.0%，進而更佳為超過5.5%，進而更佳為超過6.5%，進而更佳為超過8.5%，進而更佳為超過10.0%，進而更佳為超過15.0%。 另一方面，藉由將ZnO成分之含量設為45.0%以下，可抑制玻璃之折射率降低，且可減低因黏性過度下降所引起之失透。因此，ZnO成分之含量較佳為45.0%以下，更佳為未達40.0%，進而更佳為未達35.0%，進而更佳為未達33.0%，進而更佳為未達32.0%。 ZnO成分可使用ZnO、ZnF2 等作為原料。 ZrO2 成分於含有超過0%之情形，係可提高玻璃之折射率及阿貝數，且提高耐失透性之任意成分。因此，ZrO2 成分之含量亦較佳為超過0%，更佳為超過1.0%，進而更佳為2.0%以上，進而更佳為超過2.0%。 另一方面，藉由將ZrO2 成分之含量設為15.0%以下，可減低因過量含有ZrO2 成分而引起之失透。因此，ZrO2 成分之含量較佳為15.0%以下，更佳為未達12.0%，進而更佳為未達10.0%，進而更佳為未達6.9%，進而更佳為未達6.0%。 ZrO2 成分可使用ZrO2 、ZrF4 等作為原料。 Nb2 O5 成分於含有超過0%之情形，係藉由提高玻璃之折射率且降低玻璃之液相溫度而提高耐失透性之任意成分。 另一方面，藉由將Nb2 O5 成分之含量設為未達10.0%，而抑制玻璃之材料成本。又，可減低因過量含有Nb2 O5 成分而引起之失透，且抑制玻璃之對於可見光(尤其為波長500 nm以下)之透射率之下降。又，藉此抑制阿貝數之下降。因此，Nb2 O5 成分之含量較佳為未達10.0%，更佳為未達5.0%，進而更佳為未達3.0%，進而更佳為未達2.0%，進而更佳為未達1.4%，進而更佳為未達1.0%，進而更佳為未達0.5%，進而更佳為未達0.1%。尤其自降低材料成本之觀點而言，最佳為不含Nb2 O5 成分。 Nb2 O5 成分可使用Nb2 O5 等作為原料。 WO3 成分於含有超過0%之情形，係可降低因其他高折射率成分所致之玻璃著色，且提高折射率，降低玻璃轉移點，並提高耐失透性之任意成分。 另一方面，藉由將WO3 成分之含量設為未達10.0%，而抑制玻璃之材料成本。又，減低因WO3 成分所致之玻璃著色且提高可見光透射率。因此，WO3 成分之含量較佳為未達10.0%，更佳為未達5.0%，進而更佳為未達3.0%，進而更佳為未達1.0%，進而更佳為未達0.5%，進而更佳為未達0.1%。尤其自降低材料成本之觀點而言，最佳為不含WO3 成分。 WO3 成分可使用WO3 等作為原料。 Gd2 O3 成分及Yb2 O3 成分於含有超過0%之情形，係提高玻璃之折射率之任意成分。 然而，Gd2 O3 成分及Yb2 O3 成分因原料價格較高，若其含有量較多則生產成本變高，故減少Nb2 O5 成分或WO3 成分等所致之效果被抵消。又，藉由減低Gd2 O3 成分或Yb2 O3 成分之含量，而抑制玻璃之阿貝數之上升。因此，Gd2 O3 成分及Yb2 O3 成分之含量各較佳為未達4.0%，更佳為未達2.0%，進而更佳為未達1.0%，進而更佳為未達0.5%，進而更佳為未達0.1%。尤其自降低材料成本之觀點而言，最佳為不含該等成分。 Gd2 O3 成分及Yb2 O3 成分可使用Gd2 O3 、GdF3 、Yb2 O3 等作為原料。 Ta2 O5 成分於含有超過0%之情形，係提高玻璃之折射率且提高耐失透性之任意成分。 然而，Ta2 O5 成分因原料價格較高，若其含有量較多則生產成本變高，故減少Nb2 O5 成分或WO3 成分等所致之效果被抵消。又，藉由將Ta2 O5 成分之含量設為未達5.0%，可降低原料之熔解溫度，且降低熔解原料所需能量，故亦可降低光學玻璃之製造成本。因此，Ta2 O5 成分之含量較佳為未達5.0%，更佳為未達3.0%，進而更佳為未達1.0%，進而更佳為未達0.5%，進而更佳為未達0.1%。尤其自降低材料成本之觀點而言，最佳為不含Ta2 O5 成分。 Ta2 O5 成分可使用Ta2 O5 等作為原料。 TiO2 成分於含有超過0%之情形，係藉由提高玻璃之折射率且降低玻璃之液相溫度而提高穩定性之任意成分。因此，TiO2 成分之含量亦較佳為超過0%，更佳為超過1.1%，進而更佳為超過4.0%，進而更佳為超過5.0%，進而更佳為超過6.5%。 另一方面，藉由將TiO2 成分之含量設為未達40.0%，可降低過量含有TiO2 成分而引起之失透，且抑制玻璃對於可見光(尤其為波長500 nm以下)之透射率之下降。又，藉此抑制阿貝數之下降。因此，TiO2 成分之含量較佳為未達40.0%，更佳為未達37.0%，進而更佳為未達35.0%，進而更佳為未達30.0%，進而更佳為未達26.0%，進而更佳為未達25.0%，進而更佳為未達23.0%，進而更佳為未達20.0%，進而更佳為未達15.0%。 TiO2 成分可使用TiO2 等作為原料。 Y2 O3 成分於含有超過0%之情形，係可維持高折射率及高阿貝數，且與其他稀土類元素相比更抑制了玻璃之材料成本，且較其他稀土類成分更可減低玻璃之比重之任意成分。因此，Y2 O3 成分之含量較佳為超過0%，更佳為超過1.0%，進而更佳為超過1.5%，進而更佳為超過2.0%。 另一方面，藉由將Y2 O3 成分之含有量設為25.0%以下，而抑制玻璃之折射率下降，且提高玻璃之穩定性。又，抑制玻璃原料之熔解性惡化。因此，Y2 O3 成分之含量較佳為25.0%以下，更佳為未達20.0%，進而更佳為未達10.0%，進而更佳為未達8.0%，進而更佳為未達7.0%。 Y2 O3 成分可使用Y2 O3 、YF3 等作為原料。 MgO成分、CaO成分、SrO成分及BaO成分於含有超過0%之情形，係可調整玻璃之折射率或熔融性、耐失透性之任意成分。尤其，BaO成分亦係可提高折射率，且提高玻璃原料之熔解性之成分。因此，BaO成分之含量較佳為超過0%，更佳為超過1.0%，進而更佳為超過2.0%。 另一方面，藉由將MgO成分、CaO成分及SrO成分之含量分別設為10.0%以下，可抑制折射率下降，且可降低過量含有該等成分而引起之失透。因此，MgO成分、CaO成分及SrO成分之含量分別較佳為10.0%以下，更佳為未達5.0%，進而更佳為未達3.0%，進而更佳為未達1.0%。 又，藉由將BaO成分之含量設為25.0%以下，亦可容易獲得期望之折射率，且可減低因過量含有該等成分而引起之失透。因此，BaO成分之含量較佳為25.0%以下，更佳為未達20.0%，進而更佳為未達15.0%。 MgO成分、CaO成分、SrO成分及BaO成分可使用MgCO3 、MgF2 、CaCO3 、CaF2 、Sr(NO3 )2 、SrF2 、BaCO3 、Ba(NO3 )2 、BaF2 等作為原料。 Li2 O成分、Na2 O成分及K2 O成分於含有超過0%之情形，係可改善玻璃之熔融性，且可降低玻璃轉移點之任意成分。 另一方面，藉由將Li2 O成分、Na2 O成分及K2 O成分之各者設為10.0%以下，可使玻璃之折射率不易下降，且減低玻璃之失透。又，尤其使Li2 O成分之含量降低，藉此因玻璃之黏性提高，故可降低玻璃之紋理。因此，Li2 O成分、Na2 O成分及K2 O成分之含量分別較佳為10.0%以下，更佳為未達5.0%，進而更佳為未達3.0%，進而更佳為未達1.0%，進而更佳為未達0.5%，進而更佳為未達0.1%。 Li2 O成分、Na2 O成分及K2 O成分可使用Li2 CO3 、LiNO3 、Li2 CO3 、Na2 CO3 、NaNO3 、NaF、Na2 SiF6 、K2 CO3 、KNO3 、KF、KHF2 、K2 SiF6 等作為原料。 P2 O5 成分於含有超過0%之情形，係降低玻璃之液相溫度且提高耐失透性之任意成分。 另一方面，藉由將P2 O5 成分之含量設為10.0%以下，而抑制玻璃之化學耐久性，尤其是耐水性之下降。因此，P2 O5 成分之含有量較佳為10.0%以下，更佳為未達5.0%，進而更佳為未達3.0%。 P2 O5 成分可使用Al(PO3 )3 、Ca(PO3 )2 、Ba(PO3 )2 、BPO4 、H3 PO4 等作為原料。 GeO2 成分於含有超過0%之情形，係可提高玻璃之折射率，且提高耐失透性之任意成分。 然而，GeO2 因原料價格較高，若其含有量較多則生產成本變高，故減少Gd2 O3 成分或Ta2 O5 成分等所致之效果被抵消。因此，GeO2 成分之含量較佳為10.0%以下，更佳為未達5.0%，進而更佳為未達3.0%，進而更佳為未達1.0%，進而更佳為未達0.1%。尤其自降低材料成本之觀點而言，亦可不含GeO2 成分。 GeO2 成分可使用GeO2 等作為原料。 Al2 O3 成分及Ga2 O3 成分於含有超過0%之情形，係可提高玻璃之化學耐久性，且可提高熔融玻璃之耐失透性之任意成分。 另一方面，藉由將Al2 O3 成分及Ga2 O3 成分之各者之含量設為15.0%以下，而降低玻璃之液相溫度，且提高耐失透性。因此，Al2 O3 成分及Ga2 O3 成分之各者之含量較佳為15.0%以下，更佳為未達10.0%，進而更佳為未達5.0%，進而更佳為未達3.0%。 Al2 O3 成分及Ga2 O3 成分可使用Al2 O3 、Al(OH)3 、AlF3 、Ga2 O3 、Ga(OH)3 等作為原料。 Bi2 O3 成分於含有超過0%之情形，係提高折射率且降低玻璃轉移點之任意成分。 另一方面，藉由將Bi2 O3 成分之含量設為15.0%以下，而降低玻璃之液相溫度，且提高耐失透性。因此，Bi2 O3 成分之含量較佳為15.0%以下，更佳為未達10.0%，進而更佳為未達5.0%，進而更佳為未達3.0%，進而更佳為未達1.0%。 Bi2 O3 成分可使用Bi2 O3 等作為原料。 TeO2 成分於含有超過0%之情形，係提高折射率且降低玻璃轉移點之任意成分。 另一方面，TeO2 於以白金製之坩鍋或與熔融玻璃接觸之部分以白金形成之熔融槽來熔融玻璃原料時，有與白金合金化之問題。因此，TeO2 成分之含量較佳為15.0%以下，更佳為未達10.0%，進而更佳為未達5.0%，進而更佳為未達3.0%，進而更佳為未達1.0%。 TeO2 成分可使用TeO2 等作為原料。 SnO2 成分於含有超過0%之情形，係減低熔融玻璃之氧化並澄清，且提高玻璃之可見光透射率之任意成分。 另一方面，藉由將SnO2 成分之含量設為3.0%以下，可減低因熔融玻璃之還原而引起之玻璃著色、或玻璃之失透。又，因SnO2 成分與熔解設備(尤其Pt等之貴金屬)之合金化被減低，故謀求熔解設備之長壽命化。因此，SnO2 成分之含量較佳為3.0%以下，更佳為未達1.0%，進而更佳為未達0.5%，進而更佳為未達0.1%。 SnO2 成分可使用SnO、SnO2 、SnF2 、SnF4 等作為原料。 Sb2 O3 成分於含有超過0%之情形，係可使熔融玻璃脫泡之任意成分。 另一方面，若Sb2 O3 量過多，則可見光區域之短波長區域之透射率變差。因此，Sb2 O3 成分之含量較佳為1.0%以下，更佳為未達0.5%，進而更佳為未達0.3%。 Sb2 O3 成分可使用Sb2 O3 、Sb2 O5 、Na2 H2 Sb2 O7 ・5H2 O等作為原料。 另，使玻璃澄清且脫泡之成分並非限定於上述之Sb2 O3 成分，可使用玻璃製造領域中周知之澄清劑、脫泡劑或該等之組合。 F成分於含有超過0%之情形，係可提高玻璃之阿貝數，降低玻璃轉移點，且提高耐失透性之任意成分。 然而，若F成分之含有量，亦即作為與上述之各金屬元素之1種或2種以上之氧化物之一部分或全部置換之氟化物之F之合計量超過15.0%，則F成分之揮發量變多，因而不易獲得穩定之光學常數，且不易獲得均質之玻璃。又，阿貝數過度上升。 因此，F成分之含量較佳為15.0%以下，更佳為未達10.0%，進而更佳為未達5.0%，進而更佳為未達3.0%。 F成分可藉由使用例如ZrF4 、AlF3 、NaF、CaF2 等作為原料，而包含於玻璃內。 SiO2 成分之含量相對於B2 O3 成分之含量之比例(莫耳比)較佳為0.13以上1.70以下。 尤其，藉由將該莫耳比設為0.13以上，可容易獲得減低失透且耐於量產之穩定的玻璃。因此，莫耳比SiO2 /B2 O3 較佳為0.13以上，更佳為0.15以上，進而更佳為0.17以上，進而更佳為0.18以上，進而更佳為超過0.20，進而更佳為超過0.24，進而更佳為超過0.28，進而更佳為超過0.32。 另一方面，藉由將該莫耳比設為1.70以下，而抑制玻璃轉移點之上升。因此，莫耳比SiO2 /B2 O3 較佳為1.70以下，更佳為1.50以下，進而更佳為1.30以下，進而更佳為未達1.30，進而更佳為未達1.20，進而更佳為未達1.00，進而更佳為未達0.85，進而更佳為未達0.80，進而更佳為未達0.70。 Ta2 O5 成分、Nb2 O5 成分、WO3 成分、Gd2 O3 成分及Yb2 O3 成分之合計量(莫耳和)較佳為未達10.0%。藉此，因該等昂貴成分之含量被降低，故可抑制玻璃之材料成本。因此，莫耳和Ta2 O5 +Nb2 O5 +WO3 +Gd2 O3 +Yb2 O3 較佳為為達10.0%，更佳為未達8.0%，進而更佳為未達5.0%，進而更佳為未達3.0%，進而更佳為未達2.0%，進而更佳為未達1.0%。尤其自獲得材料成本低廉之玻璃之觀點而言，進而較佳將莫耳和Ta2 O5 +Nb2 O5 +WO3 +Gd2 O3 +Yb2 O3 設為未達0.1%，最佳係設為0%。 ZnO成分之含量相對於La2 O3 成分及Y2 O3 成分之含量之比例(莫耳比)較佳為0.10以上4.00以下。 尤其，藉由將該莫耳比設為0.10以上，可提高玻璃原料之熔解性，且容易獲得更穩定之玻璃。因此，莫耳比ZnO/(La2 O3 +Y2 O3 )較佳以0.10，更佳以0.15，進而更佳以0.20，進而更佳以0.24為下限，進而更佳為超過0.26，進而更佳以0.27，進而更佳以0.32，進而更佳以0.35為下限。 另一方面，藉由將該莫耳比設為4.00以下，可降低液相溫度，且可降低因玻璃轉移點過度下降而引起之失透。因此，莫耳比ZnO/(La2 O3 +Y2 O3 )較佳以4.00，更佳以3.50，進而更佳以3.00，進而更佳以2.50為上限。 Ln2 O3 成分(式中，Ln係選自由La、Gd、Y、Yb、Lu所組成之群中之1種以上)之含量之和(莫耳和)較佳為5.0%以上40.0%以下。 尤其，藉由將該和設為5.0%以上，因玻璃之折射率及阿貝數提高，故可容易獲得具有期望之折射率及阿貝數之玻璃。因此，Ln2 O3 成分之莫耳和較佳為5.0%以上，更佳為超過8.0%，進而更佳為超過10.0%，進而更佳為超過11.0%，進而更佳為超過12.0%。 另一方面，藉由將其和設為40.0%以下，因玻璃之液相溫度變低，故可減低玻璃之失透。又，抑制阿貝數之過度上升。因此，Ln2 O3 成分之莫耳和較佳為40.0%以下，更佳為未達35.0%，進而更佳為未達30.0%，進而更佳為未達27.0%，進而更佳為未達25.0%，進而更佳為未達22.0%，進而更佳為未達20.0%，進而更佳為未達18.0%，進而更佳為未達16.5%。 尤其，於第3光學玻璃中，藉由含有CaO成分及BaO成分中至少一者，即便以更少之Ln2 O3 成分含量，亦可獲得期望之高折射率之玻璃，故可進而減低玻璃之材料成本。 RO成分(式中，R係選自由Mg、Ca、Sr、Ba所組成之群中之1種以上)之含量之和(莫耳和)較佳為25.0%以下。藉此，抑制折射率之下降，又，提高玻璃之穩定性。因此，RO成分之莫耳和較佳為25.0%以下，更佳為未達20.0%，進而更佳為未達15.0%。 另一方面，RO成分之莫耳和亦較佳為超過0%，更佳為超過1.0%，進而更佳為超過2.0%。 Rn2 O成分(式中，Rn係選自由Li、Na、K所組成之群中之1種以上)之含量之和(莫耳和)較佳為10.0%以下。藉此，可抑制熔融玻璃之黏性下降，且不易使玻璃之折射率下降，且可減低玻璃之失透。因此，Rn2 O成分之莫耳和較佳為10.0%以下，更佳為未達5.0%，進而更佳為未達3.0%，進而更佳為未達1.0%，進而更佳為未達0.5%，進而更佳為未達0.1%。 RO成分(式中，R係選自由Mg、Ca、Sr、Ba所組成之群中之1種以上)及ZnO成分之合計含量相對於Ln2 O3 成分(式中，Ln係選自由La、Gd、Y、Yb、Lu所組成之群中之1種以上)之合計含量之比例(莫耳比)較佳為超過0.30。 藉此，可更進一步減低玻璃之材料成本，且提高玻璃之穩定性。因此，莫耳比(RO+ZnO)/Ln2 O3 較佳為超過0.30，更佳為超過0.45，進而更佳為超過0.50，進而更佳為超過0.80，進而更佳為超過1.00。 另一方面，基於抑制折射率下降之觀點，該莫耳比較佳為未達7.00，更佳為未達5.00，進而更佳為未達4.00。 BaO成分之含量相對於ZnO成分之含量之比例(莫耳比)較佳為5.00以下。藉此，提高玻璃原料之熔融性與玻璃之穩定性。因此，莫耳比BaO/ZnO較佳以5.00，更佳以4.00，進而更佳以3.00，進而更佳以2.80，進而更佳以2.50為上限。 BaO成分之含量相對於RO成分(式中，R係選自由Mg、Ca、Sr、Ba所組成之群中之1種以上)之合計含量之比例(莫耳比)較佳為0.50以上。藉此，提高玻璃之折射率。因此，莫耳比BaO/RO亦較佳以0.50，更佳以0.70，進而更佳以0.80為下限。 另，該莫耳比之上限亦可為1.00。 ＜關於不應含有之成分＞ 其次，對本發明之光學玻璃中不應含有之成分、及含有較不佳之成分進行說明。 在不損及本申請案發明之玻璃特性之範圍內可根據需要添加其他成分。但Ti、Zr、Nb、W、La、Gd、Y、Yb、Lu除外，V、Cr、Mn、Fe、Co、Ni、Cu、Ag及Mo等之各過渡金屬成分於各自單獨或複合而少量含有之情形時亦具有使玻璃著色，且對可見光區域之特定波長產生吸收之性質，因而尤其於使用可見光區域之波長之光學玻璃中，較佳實質上不包含。 又，PbO等之鉛化合物及As2 O3 等之砷化合物係環境負荷較高之成分，因而期望實質上不含有，即，除不可避免地混入以外，較好一概不含有。 再者，Th、Cd、Tl、Os、Be、及Se之各成分係近年來有作為有害化學物質而控制使用之傾向，不僅是玻璃之製造步驟，且至加工步驟、及製品化後之處理之前，必須採取環境上的對策措施。因此，在重視環境上之影響之情形，較佳為實質性不含有該等。 [製造方法] 本發明之光學玻璃係例如藉以下方式製作。即，將上述原料以各成分成為特定含量之範圍內之方式均一混合，將製作之混合物投入白金坩鍋，根據玻璃原料之熔解難易度以電爐於1100～1500 ℃之溫度範圍熔解2～5小時並攪拌均質化後，下降至適當溫度，而後澆注入模具，並緩冷，藉此製作。 此時，較佳使用熔解性高者作為玻璃原料。藉此，因可以更低溫熔解，或以更短時間熔解，故可提高玻璃之生產性，且減低生產成本。又，因成分之揮發或與坩堝等之反應被降低，故可容易獲得著色較少之玻璃。 [物性] 本發明之光學玻璃較佳具有高折射率及高阿貝數(低分散)。 本發明之光學玻璃之折射率(nd )較佳以1.70，更佳以1.72，進而更佳以1.74，進而更佳以1.75，進而更佳以1.78，進而更佳以1.80為下限。尤其，第1光學玻璃之折射率(nd )亦較佳以1.75，更佳以1.78，進而更佳以1.79，進而更佳以1.80為下限。 另一方面，該折射率(nd )亦較佳以2.10，更佳以2.00，進而更佳以1.90，進而更佳以1.85為上限。尤其，第2光學玻璃之折射率(nd )亦較佳以1.90，更佳以1.88，進而更佳以1.85為上限。 本發明之光學玻璃之阿貝數(νd )較佳以25，更佳以27，進而更佳以28，進而更佳以30，進而更佳以32為下限。 另一方面，該阿貝數(νd )較佳以50，更佳以48，進而更佳以45，進而更佳以43，進而更佳以42，進而更佳以41，進而更佳以40.5為上限。尤其，第1光學玻璃之阿貝數(νd )亦較佳以48，更佳以45，進而更佳以43，進而更佳以41為上限。 藉由具有此種高折射率，即便謀求光學元件之薄型化，亦可獲得較大之光折射量。又，藉由具有此種低分散，於作為單透鏡使用時，可縮小光之波長引起之焦點偏移(色像差)。因此，於例如與具有高分散(低阿貝數)之光學元件組合而構成光學系統之情形，可作為該光學系統之整體使像差減低並謀求高成像特性等。 如此，本發明之光學玻璃於光學設計上有用，尤其於構成光學系統時，可謀求高成像特性等，且謀求光學系統之小型化，並擴大光學設計之自由度。 本發明之光學玻璃較佳為耐失透性較高，具體而言係具有低液相溫度。即，本發明之光學玻璃之液相溫度較佳以1200 ℃，更佳以1150 ℃，進而更佳以1100 ℃為上限。藉此，即便以更低溫度流出熔解後之玻璃，亦因所製作之玻璃之結晶化被減低，故可減低自熔融狀態形成玻璃時之失透，且可減低對使用玻璃之光學元件之光學特性之影響。又，因即便降低玻璃之熔解溫度亦可成形玻璃，故藉由抑制玻璃成形時消耗之能量，可降低玻璃之製造成本。另一方面，本發明之光學玻璃之液相溫度之下限並未特別限定，藉由本發明所得之玻璃之液相溫度大多約為800 ℃以上，具體而言，為850 ℃以上，進而具體而言，為900 ℃以上。另，本說明書中的「液相溫度」係表示於50 ml容量之白金製坩堝中，將30 cc之碎玻璃狀之玻璃試料置入白金坩堝中，以1250 ℃加熱成完全熔融狀態，並降溫至特定溫度保持1小時，取出至爐外冷卻後立即觀察玻璃表面及玻璃中有無結晶時，未見到結晶之最低溫度。此處降溫時之特定溫度係1200 ℃～800 ℃之間每10 ℃之溫度。 本發明之光學玻璃較佳為可見光透射率，尤其可見光中短波長側之光之透射率較高，藉此著色較少。 本發明之光學玻璃中以厚度10 mm之樣品顯示分光透射率80%之波長(λ80 )亦較佳以550 nm，更佳以520 nm，進而更佳以500 nm為上限。 本發明之光學玻璃中以厚度10 mm之樣品顯示分光透射率70%之波長(λ70 )亦較佳以500 nm，更佳以450 nm，進而更佳以420 nm，進而更佳以400 nm為上限。 本發明之光學玻璃中以厚度10 mm之樣品顯示分光透射率5%之最短波長(λ5 )亦較佳以400 nm，更佳以380 nm，進而更佳以360 nm為上限。 藉由該等，玻璃之吸收端位於紫外區域或其附近，玻璃對於可見光之透明性提高，因而可較佳地將該光學玻璃用於透鏡等之使光透射之光學元件。 本發明之光學玻璃較佳具有700 ℃以下之玻璃轉移點(Tg)。 藉此，光學玻璃具有700 ℃以下之玻璃轉移點，藉此玻璃因以更低之溫度軟化，故即便將光學玻璃用於壓製成形之情形，亦可以更低之溫度容易使玻璃壓製成形。因此，本發明之光學玻璃之玻璃轉移點較佳為700 ℃以下，更佳為650 ℃以下，進而更佳為630 ℃以下。 另一方面，光學玻璃之玻璃轉移點亦可為500 ℃以上。藉此，因玻璃之穩定性提高且不易引起結晶化，因而可減低玻璃製作時或壓製成形時之失透，藉此獲得適於壓製成形之玻璃。因此，本發明之光學玻璃之玻璃轉移點亦較佳為500 ℃以上，更佳為530 ℃以上，進而更佳為550 ℃以上。 本發明之光學玻璃較佳具有800 ℃以下之屈伏點(At)。屈伏點係與玻璃轉移點同樣地表示玻璃之軟化性之指標之一，係表示接近壓製成形溫度之溫度的指標。因此，藉由使用屈伏點為800 ℃以下之玻璃，即便將光學玻璃用於壓製成形之情形，亦可以更低之溫度容易使玻璃壓製成形。因此，本發明之光學玻璃之屈伏點較佳以800 ℃，更佳以750 ℃，進而更佳以700 ℃為上限。 另，本發明之光學玻璃之屈伏點並未特別限定，亦較佳以500 ℃，更佳以550 ℃，進而更佳以600 ℃為下限。 本發明之光學玻璃之比重較小較佳。更具體而言，本發明之光學玻璃之比重為5.00以下。藉此，因光學元件或使用其之光學機器之質量降低，故有助於光學機器之輕量化。因此，本發明之光學玻璃之比重較佳以5.00，更佳以4.70，進而更佳以4.50為上限。另，本發明之光學玻璃之比重大多為約3.00以上，更詳細而言，為3.30以上，進而詳細而言，為3.50以上。 本發明之光學玻璃之比重基於日本光學玻璃工業會規格JOGIS05-1975「光學玻璃之比重之測定方法」而測定。 本發明之光學玻璃之平均線膨脹係數(α)較小較佳。尤其，本發明之光學玻璃之平均線膨脹係數較佳以100×10-7 K-1 ，更佳以9×10-7 K-1 ，進而更佳以80×10-7 K-1 為上限。藉此，於以成形模對光學玻璃壓製成形時，因玻璃之溫度變化而引起之膨脹或收縮之總量減低。因此，於壓製成形時不易使光學玻璃破裂，可提高光學元件之生產性。 [預成形材及光學元件] 可由所製作之光學玻璃，使用例如研磨加工之方法，或再熱壓製成形或精密壓製成形等之模具壓製成形之方法，製作玻璃成形體。即，可對光學玻璃進行研削及研磨等之機械加工而製作玻璃成形體，或由光學玻璃製作模具壓製成形用之預成形材，且對該預成形材進行再熱壓製成形後進行研磨加工而製作玻璃成形體，或對進行研磨加工製作之預成形材或藉由周知之浮起成形等成形之預成形材進行精密壓製成形而製作玻璃成形體。另，製作玻璃成形體之方法並未限定於該等方法。 如此，本發明之光學玻璃可用於各種光學元件及光學設計。其中，尤其較佳的是，由本發明之光學玻璃形成預成形材，使用該預成形材進行再熱壓製成形或精密壓製成形等，製作透鏡或稜鏡等之光學元件。藉此，因徑較大之預成形材之形成變得可能，故可謀求光學元件之大型化，且用於相機或投影機等之光學機器時可實現高精細且高精度之成像特性及投影特性。 [實施例] 於表1～表26中顯示本發明之實施例(No.A1～No.A73、No.B1～No.B78、No.C1～No.C38、No.D1～No.D6)及比較例(No.X)之組成、以及該等玻璃之折射率(nd )、阿貝數(νd )、玻璃轉移點(Tg)、屈伏點(At)、液相溫度、表示分光透射率為5%、70%、80%之波長(λ5 、λ70 、λ80 )、比重及平均線膨脹係數(α)之結果。此處，實施例(No.A1～No.A73、No.D1～No.D6)係主要作為第1光學玻璃之實施例者。又，實施例(No.B1～No.B78、No.D1～No.D6)係主要作為第2光學玻璃之實施例者。又，實施例(No.C1～No.C38)係主要作為第3光學玻璃之實施例者。 另，以下實施例終歸以例示為目的，並非僅限定於該等實施例者。 本發明之實施例及比較例之玻璃均係選定各相當之氧化物、氫氧化物、碳酸鹽、硝酸鹽、氟化物、氫氧化物、偏磷酸化合物等之通常之光學玻璃所使用之高純度原料作為各成分之原料，且按表所示之各實施例之組成比例稱量且均一混合後，投入白金坩堝，根據玻璃原料之熔解難易度以電爐於1100～1500 ℃之溫度範圍內熔解2～5小時後，攪拌均質化，而後澆注入模具等，並緩冷而製作。 此處，實施例及比較例之玻璃之折射率(nd )及阿貝數(νd )係基於日本光學玻璃工業會規格JOGIS01-2003而測定。此處，折射率(nd )、阿貝數(νd )係對將緩冷降溫速度設為-25 ℃/hr而得之玻璃進行測定而求得。 實施例及比較例之玻璃之玻璃轉移點(Tg)及屈伏點(At)係藉由使用橫型膨脹測定器進行測定而求得。此處，進行測定時之樣品係使用φ4.8 mm，長度50～55 mm者，且將升溫速度設為4 ℃/min。 實施例及比較例之玻璃之透射率係基於日本光學玻璃工業會規格JOGIS02而測定。另，於本發明中，藉由測定玻璃之透射率，而求得玻璃著色之有無與程度。具體而言，對厚度10±0.1 mm之對面平行研磨品，根據JISZ8722，測定200～800 nm之分光透射率，求得λ5 (透射率5%時之波長)、λ70 (透射率70%時之波長)、λ80 (透射率80%時之波長)。 實施例及比較例之玻璃之液相溫度係於50 ml容量之白金製坩堝中，將30 cc之碎玻璃狀之玻璃試料置入白金坩堝中，以1250 ℃加熱成完全熔融狀態，並降溫至1200 ℃～800 ℃中每10 ℃設定之任意溫度並保持1小時，取出至爐外冷卻後立即觀察玻璃表面及玻璃中有無結晶時，求出未見到結晶之最低溫度。 實施例及比較例之玻璃之比重基於日本光學玻璃工業會規格JOGIS05-1975「光學玻璃之比重之測定方法」而測定。 實施例及比較例之玻璃之平均線膨脹係數(α)係根據日本光學玻璃工業會規格JOGIS08-2003「光學玻璃之熱膨脹之測定方法」，求得-30～+70 ℃中平均線膨脹係數。   [表1]

Figure 105136050-A0304-0001
[表2]
Figure 105136050-A0304-0002
 [表3]
Figure 105136050-A0304-0003
 [表4]
Figure 105136050-A0304-0004
 [表5]
Figure 105136050-A0304-0005
 [表6]
Figure 105136050-A0304-0006
 [表7]
Figure 105136050-A0304-0007
 [表8]
Figure 105136050-A0304-0008
 [表9]
Figure 105136050-A0304-0009
 [表10]
Figure 105136050-A0304-0010
 [表11]
Figure 105136050-A0304-0011
 [表12]
Figure 105136050-A0304-0012
 [表13]
Figure 105136050-A0304-0013
 [表14]
Figure 105136050-A0304-0014
 [表15]
Figure 105136050-A0304-0015
 [表16]
Figure 105136050-A0304-0016
 [表17]
Figure 105136050-A0304-0017
 [表18]
Figure 105136050-A0304-0018
 [表19]
Figure 105136050-A0304-0019
 [表20]
Figure 105136050-A0304-0020
 [表21]
Figure 105136050-A0304-0021
 [表22]
Figure 105136050-A0304-0022
 [表23]
Figure 105136050-A0304-0023
 [表24]
Figure 105136050-A0304-0024
 [表25]
Figure 105136050-A0304-0025
 [表26]
Figure 105136050-A0304-0026
 如表所示，本發明之實施例之光學玻璃因莫耳和(Nb2 O5 +WO3 )未達10.0%，故可更便宜地獲得。另一方面，比較例(No.X)之玻璃係因莫耳和(Nb2 O5 +WO3 )為11.53%，故材料成本較高者。 本發明之實施例之光學玻璃係折射率(nd )均為1.70以上，且為期望範圍內。尤其，實施例(No.A1～No.A73、No.D1～No.D6)之光學玻璃係折射率(nd )均為1.75以上，更詳細而言係1.78以上。又，實施例(No.B1～No.B78)之光學玻璃係折射率(nd )均為1.74以上。又，實施例(No.C1～No.C38)之光學玻璃係折射率(nd )均為1.80以上。 另一方面，本發明之實施例之光學玻璃係折射率(nd )均為2.10以下。尤其，實施例(No.A1～No.A73、No.D1～No.D6)之光學玻璃係折射率(nd )均為2.00以下。又，實施例(No.B1～No.B78、No.D1～No.D6)之光學玻璃係折射率(nd )均為1.90以下。又，實施例(No.C1～No.C38)之光學玻璃係折射率(nd )均為2.00以下。 本發明之實施例之光學玻璃係阿貝數(νd )均為50以下，且係期望範圍內。尤其，實施例(No.A1～No.A73、No.D1～No.D6)之光學玻璃係阿貝數(νd )均為48以下，更詳細而言為45以下。又，實施例(No.C1～No.C38)之光學玻璃係阿貝數(νd )均為41以下。 另一方面，本發明之實施例之光學玻璃係阿貝數(νd )均為25以上，且係期望範圍內。尤其，實施例(No.A1～No.A73、No.D1～No.D6)之光學玻璃係阿貝數(νd )均為26以上。又，實施例(No.B1～No.B78、No.D1～No.D6)之光學玻璃係阿貝數(νd )均為30以上，更詳細而言為32以上。又，實施例(No.C1～No.C38)之光學玻璃係阿貝數(νd )均為26以上。 又，本發明之光學玻璃係形成穩定玻璃，且於玻璃製作時不易引起失透者。此推測係因本發明之光學玻璃之液相溫度為1250 ℃以下，更詳細而言為1210 ℃以下之故。 又，本發明之實施例之光學玻璃係λ80 (透射率80%時之波長)均為550 nm以下，更詳細而言為490 nm以下。 又，本發明之實施例之光學玻璃係λ70 (透射率70%時之波長)均為500 nm以下，更詳細而言為490 nm以下。尤其，實施例(No.C1～No.C38)之光學玻璃係λ70 均為450 nm以下。 又，本發明之實施例之光學玻璃係λ5 (透射率5%時之波長)均為400 nm以下，更詳細而言為380 nm以下，且係期望範圍內。尤其，實施例(No.C1～No.C38)之光學玻璃係λ5 均為370 nm以下。 因此，可了解本發明之實施例之光學玻璃係折射率(nd )及阿貝數(νd )在期望範圍內，且可見光短波長之透射率高，耐失透性高。 除此之外，本發明之實施例之光學玻璃係玻璃轉移點(Tg)為700 ℃以下，更詳細而言為620 ℃以下。 又，本發明之實施例之光學玻璃係屈伏點(At)為800 ℃以下，更詳細而言為670 ℃以下。 基於該等，亦可推測本發明之實施例之光學玻璃係玻璃轉移點或屈伏點低。 又，本發明之實施例之光學玻璃係比重均為5.00以下，更詳細而言為4.50以下。尤其，本發明之實施例(No.B1～No.B78、No.D1～No.D6)之光學玻璃係比重均為4.50以下。 又，實施例之光學玻璃係平均線膨脹係數(α)為100×10-7 K-1 以下，更詳細而言為80×10-7 K-1 以下。 再者，使用本發明之實施例之光學玻璃，形成玻璃塊，且對該玻璃塊進行研削及研磨，加工成透鏡及稜鏡之形狀。其結果，可加工成穩定之多種透鏡及稜鏡之形狀。 以上，雖對本發明以例示之目的進行詳細說明，但本發明僅基於例示之目的，熟知本技藝者當可理解在未脫離本發明之思想及範圍內可進行多種改變。The optical glass of the present invention contains 5.0% or more and 55.0% or less of B 2 O 3 component, and 5.0% or more and 30.0% or less of La 2 O 3 component in molar %, and the molar and (Nb 2 O 5 +WO 3 ) Less than 10.0%, with a refractive index (n d ) above 1.70, and an Abbe number (ν d ) above 25 and below 50. By using the B 2 O 3 component and the La 2 O 3 component as the basis, it is easy to obtain a stable glass having a refractive index (n d ) of 1.70 or more and an Abbe number (ν d ) of 25 or more and 50 or less. In addition, the inventor of the present application found that, especially in glasses with a refractive index (n d ) above 1.70 and an Abbe number (ν d ) above 25 and below 50, the components that make the material cost higher, especially Nb 2 O When the content of 5 components or WO 3 components is reduced, the liquidus temperature of the glass is also lowered, and the devitrification can be reduced especially when the glass is made. Therefore, it is possible to obtain an optical glass with refractive index (n d ) and Abbe number (ν d ) within the desired range at a lower cost, and with high devitrification resistance. In addition, since the optical glass of the present invention has a high transmittance with respect to visible light, it can be preferably used for the purpose of transmitting visible light. Among them, one having a refractive index (n d ) of 1.75 or more and an Abbe number (ν d ) of 25 or more and 48 or less can also be used as the first optical glass. In addition, a refractive index (n d ) of 1.70 or more and 1.90 or less and an Abbe number (ν d ) of 30 or more and 50 or less may be used as the second optical glass. In addition, at least one of the CaO component and the BaO component may be contained in a total of more than 0% and 30.0% or less as the third optical glass. By containing at least one of the CaO component and the BaO component, it is easy to obtain a more stable glass having a refractive index (n d ) of 1.70 or more and an Abbe number (ν d ) of 25 or more and 50 or less. Moreover, especially by containing at least one of a CaO component and a BaO component, a desired high refractive index is obtained and the transmittance of light on the short-wavelength side of visible light is improved. In addition to the Nb 2 O 5 component or the WO 3 component, by reducing the total amount of rare earths, further cost reduction can be achieved. Hereinafter, the embodiment of the optical glass of the present invention will be described in detail. The present invention does not limit the following embodiments in any way, and can be implemented by adding appropriate changes within the scope of the object of the present invention. In addition, although appropriate descriptions may be omitted for overlapping descriptions, this does not limit the gist of the invention. [Glass component] The composition range of each component constituting the optical glass of the present invention will be described below. In this specification, unless otherwise specified, the content of each component is expressed in mole% relative to the total mole% of the total composition converted from all oxides. Here, the "oxide conversion composition" assumes that the oxides, composite salts, metal fluorides, etc. used as the raw materials of the glass components of the present invention are all decomposed and converted into oxides when they are melted. The total mole number of the object is set to 100 mole%, and the composition of each component contained in the glass is described. <Regarding essential components and optional components> The B 2 O 3 component is an essential component of the glass-forming oxide in the optical glass of the present invention containing a large amount of rare earth oxides. In particular, by setting the content of the B 2 O 3 component to 5.0% or more, the devitrification resistance of the glass is improved, and the Abbe number of the glass is increased. Therefore, the content of the B 2 O 3 component is preferably 5.0% or more, more preferably 10.0% or more, still more preferably more than 10.0%, still more preferably more than 14.0%, still more preferably 15.0% or more, and still more preferably It is more than 15.0%, more preferably more than 19.0%, still more preferably more than 20.0%, still more preferably more than 20.0%, still more preferably more than 25.0%. On the other hand, by setting the content of the B 2 O 3 component to 55.0% or less, a larger refractive index can be easily obtained, and deterioration of chemical durability can be suppressed. Therefore, the content of the B 2 O 3 component is preferably 55.0% or less, more preferably less than 51.0%, still more preferably 50.0% or less, still more preferably less than 47.0%, still more preferably less than 45.0%, Even more preferably, it is less than 42.0%, even more preferably, it is less than 40.0%, and even more preferably, it is less than 38.0%. For the B 2 O 3 component system, H 3 BO 3 , Na 2 B 4 O 7 , Na 2 B 4 O 7 ·10H 2 O, BPO 4, etc. can be used as raw materials. The La 2 O 3 component is an essential component to increase the refractive index and Abbe number of the glass. Therefore, the content of the La 2 O 3 component is preferably 5.0% or more, more preferably more than 7.0%, still more preferably more than 8.0%, and still more preferably more than 10.0%. On the other hand, by setting the content of the La 2 O 3 component to 30.0% or less, it is possible to reduce the devitrification by improving the stability of the glass, and to suppress an excessive increase in the Abbe number. In addition, the meltability of the glass raw material is improved. Therefore, the content of the La 2 O 3 component is preferably 30.0% or less, more preferably less than 25.0%, still more preferably less than 22.0%, still more preferably less than 21.0%, and still more preferably less than 20.0% , Still more preferably 19.5% or less, still more preferably 17.5% or less, still more preferably 16.5% or less, still more preferably 14.5% or less. For the La 2 O 3 component, La 2 O 3 , La(NO 3 ) 3 ·XH 2 O (X is an arbitrary integer), etc. can be used as raw materials. The total amount of the Nb 2 O 5 component and the WO 3 component is preferably set to less than 10.0%. Thereby, since the content of these expensive components is reduced, the material cost of the glass can be suppressed. Therefore, the molar sum (Nb 2 O 5 +WO 3 ) is preferably less than 10.0%, more preferably less than 5.0%, still more preferably less than 3.0%, still more preferably less than 2.0%, and still more Preferably, it is less than 1.5%, more preferably less than 1.0%, still more preferably less than 0.5%, and still more preferably less than 0.1%. At least one of the CaO component and the BaO component preferably contains more than 0% and 30.0% or less in total. In particular, by setting the sum to more than 0%, the refractive index or visible light transmittance of the glass is increased. In addition, since this reduces the content of rare earths, it is also possible to further reduce costs. Therefore, the molar sum (CaO+BaO) is preferably more than 0%, more preferably more than 1.0%, and still more preferably more than 2.0%. On the other hand, by setting the sum to 30.0% or less, since the liquidus temperature of the glass becomes lower, the devitrification of the glass can be reduced. Therefore, the molar sum (CaO+BaO) is preferably 30.0% or less, more preferably less than 25.0%, still more preferably less than 20.0%, and still more preferably less than 15.0%. When the SiO 2 component contains more than 0%, it is an optional component that can increase the viscosity of the molten glass and reduce the coloring of the glass. In addition, it is also a component that makes it easy to obtain glass that has improved stability of the glass and is resistant to mass production. Therefore, the content of the SiO 2 component is also preferably more than 0%, more preferably more than 1.0%, still more preferably more than 5.0%, still more preferably more than 8.0%, still more preferably more than 10.2%, and still more preferably More than 10.5%. On the other hand, by setting the content of the SiO 2 component to 25.0% or less, the increase in the glass transition point is suppressed, and the decrease in the refractive index is suppressed. Therefore, the content of the SiO 2 component is preferably 25.0%, more preferably less than 22.0%, still more preferably less than 20.0%, still more preferably less than 18.0%, still more preferably less than 15.5%, and still more The best is less than 14.0%. As the SiO 2 component, SiO 2 , K 2 SiF 6 , Na 2 SiF 6 or the like can be used as a raw material. When the ZnO component contains more than 0%, it is an optional component that improves the solubility of the raw materials, promotes the defoaming of self-melting glass, and improves the stability of the glass. In addition, it is also possible to reduce the coloring components of the glass by shortening the melting time. In addition, it is also a component that can reduce the glass transition point and improve chemical durability. Therefore, the content of the ZnO component is also preferably more than 0%, more preferably more than 1.0%, still more preferably more than 2.2%, still more preferably more than 2.5%, still more preferably more than 4.2%, and still more preferably more than 4.5%, still more preferably more than 5.0%, still more preferably more than 5.5%, still more preferably more than 6.5%, still more preferably more than 8.5%, still more preferably more than 10.0%, still more preferably more than 15.0% . On the other hand, by setting the content of the ZnO component to 45.0% or less, the decrease in the refractive index of the glass can be suppressed, and the devitrification caused by the excessive decrease in viscosity can be reduced. Therefore, the content of the ZnO component is preferably 45.0% or less, more preferably less than 40.0%, still more preferably less than 35.0%, still more preferably less than 33.0%, and still more preferably less than 32.0%. As the ZnO component, ZnO, ZnF 2 or the like can be used as a raw material. When the ZrO 2 component contains more than 0%, it is an optional component that can increase the refractive index and Abbe number of the glass, and improve the devitrification resistance. Therefore, the content of the ZrO 2 component is also preferably more than 0%, more preferably more than 1.0%, still more preferably more than 2.0%, and still more preferably more than 2.0%. On the other hand, by setting the content of the ZrO 2 component to 15.0% or less, it is possible to reduce the devitrification caused by excessively containing the ZrO 2 component. Therefore, the content of the ZrO 2 component is preferably 15.0% or less, more preferably less than 12.0%, still more preferably less than 10.0%, still more preferably less than 6.9%, and still more preferably less than 6.0%. As the ZrO 2 component, ZrO 2 , ZrF 4, etc. can be used as a raw material. When the Nb 2 O 5 component contains more than 0%, it is an optional component that improves the resistance to devitrification by increasing the refractive index of the glass and lowering the liquidus temperature of the glass. On the other hand, by setting the content of the Nb 2 O 5 component to less than 10.0%, the material cost of the glass is suppressed. In addition, it can reduce the devitrification caused by excessively containing the Nb 2 O 5 component, and suppress the drop in the transmittance of the glass to visible light (especially the wavelength of 500 nm or less). In addition, this suppresses the decrease in Abbe number. Therefore, the content of the Nb 2 O 5 component is preferably less than 10.0%, more preferably less than 5.0%, still more preferably less than 3.0%, still more preferably less than 2.0%, and still more preferably less than 1.4 %, still more preferably less than 1.0%, still more preferably less than 0.5%, still more preferably less than 0.1%. In particular, from the viewpoint of reducing material cost, it is most preferable that the Nb 2 O 5 component is not contained. For the Nb 2 O 5 component, Nb 2 O 5 or the like can be used as a raw material. When the WO 3 component contains more than 0%, it is an optional component that can reduce the coloring of the glass due to other high refractive index components, increase the refractive index, reduce the glass transition point, and improve the resistance to devitrification. On the other hand, by setting the content of the WO 3 component to less than 10.0%, the material cost of the glass is suppressed. In addition, it reduces the coloring of the glass due to the WO 3 component and improves the visible light transmittance. Therefore, the content of the WO 3 component is preferably less than 10.0%, more preferably less than 5.0%, still more preferably less than 3.0%, still more preferably less than 1.0%, and still more preferably less than 0.5%, More preferably, it is less than 0.1%. In particular, from the viewpoint of reducing material cost, it is most preferable not to contain WO 3 components. For the WO 3 component, WO 3 or the like can be used as a raw material. When the content of Gd 2 O 3 and Yb 2 O 3 exceeds 0%, it is an optional component that increases the refractive index of the glass. However, since the Gd 2 O 3 component and the Yb 2 O 3 component are expensive in raw materials, the production cost becomes higher if they are contained in a large amount, so the effect of reducing the Nb 2 O 5 component or the WO 3 component is cancelled out. In addition, by reducing the content of the Gd 2 O 3 component or the Yb 2 O 3 component, the increase in the Abbe number of the glass is suppressed. Therefore, the content of each of the Gd 2 O 3 component and the Yb 2 O 3 component is preferably less than 4.0%, more preferably less than 2.0%, still more preferably less than 1.0%, and still more preferably less than 0.5%, More preferably, it is less than 0.1%. Especially from the viewpoint of reducing material cost, it is best not to contain these components. For the Gd 2 O 3 component and the Yb 2 O 3 component, Gd 2 O 3 , GdF 3 , Yb 2 O 3, etc. can be used as raw materials. When the Ta 2 O 5 component contains more than 0%, it is an optional component that increases the refractive index of the glass and improves the resistance to devitrification. However, the Ta 2 O 5 component has a high raw material price, and if its content is large, the production cost becomes high. Therefore, the effect of reducing the Nb 2 O 5 component or the WO 3 component is canceled. In addition, by setting the content of the Ta 2 O 5 component to less than 5.0%, the melting temperature of the raw material can be lowered, and the energy required for melting the raw material can be reduced, so the manufacturing cost of the optical glass can also be reduced. Therefore, the content of the Ta 2 O 5 component is preferably less than 5.0%, more preferably less than 3.0%, still more preferably less than 1.0%, still more preferably less than 0.5%, and still more preferably less than 0.1 %. In particular, from the viewpoint of reducing material cost, it is most preferable that the Ta 2 O 5 component is not contained. For the Ta 2 O 5 component, Ta 2 O 5 or the like can be used as a raw material. When the TiO 2 component contains more than 0%, it is an optional component that improves the stability by increasing the refractive index of the glass and lowering the liquidus temperature of the glass. Therefore, the content of the TiO 2 component is also preferably more than 0%, more preferably more than 1.1%, still more preferably more than 4.0%, still more preferably more than 5.0%, and still more preferably more than 6.5%. On the other hand, by setting the content of the TiO 2 component to less than 40.0%, the devitrification caused by excessive TiO 2 content can be reduced, and the decrease in the transmittance of the glass to visible light (especially with a wavelength of 500 nm or less) can be suppressed. . In addition, this suppresses the decrease in Abbe number. Therefore, the content of the TiO 2 component is preferably less than 40.0%, more preferably less than 37.0%, still more preferably less than 35.0%, still more preferably less than 30.0%, and still more preferably less than 26.0%, It is still more preferably less than 25.0%, still more preferably less than 23.0%, still more preferably less than 20.0%, and still more preferably less than 15.0%. As the TiO 2 component, TiO 2 or the like can be used as a raw material. When the Y 2 O 3 component contains more than 0%, it can maintain a high refractive index and a high Abbe number. Compared with other rare earth elements, the material cost of glass is suppressed, and it can be reduced compared with other rare earth components. Any component of the specific gravity of the glass. Therefore, the content of the Y 2 O 3 component is preferably more than 0%, more preferably more than 1.0%, still more preferably more than 1.5%, and still more preferably more than 2.0%. On the other hand, by setting the content of the Y 2 O 3 component to 25.0% or less, the decrease in the refractive index of the glass is suppressed, and the stability of the glass is improved. In addition, the deterioration of the melting properties of the glass raw materials is suppressed. Therefore, the content of the Y 2 O 3 component is preferably 25.0% or less, more preferably less than 20.0%, still more preferably less than 10.0%, still more preferably less than 8.0%, and still more preferably less than 7.0% . For the Y 2 O 3 component, Y 2 O 3 , YF 3, etc. can be used as raw materials. When the MgO component, CaO component, SrO component, and BaO component contain more than 0%, they are optional components that can adjust the refractive index, meltability, and devitrification resistance of the glass. In particular, the BaO component is also a component that can increase the refractive index and improve the solubility of the glass raw material. Therefore, the content of the BaO component is preferably more than 0%, more preferably more than 1.0%, and still more preferably more than 2.0%. On the other hand, by setting the contents of the MgO component, CaO component, and SrO component to 10.0% or less, the decrease in refractive index can be suppressed, and devitrification caused by excessive inclusion of these components can be reduced. Therefore, the contents of the MgO component, the CaO component, and the SrO component are each preferably 10.0% or less, more preferably less than 5.0%, still more preferably less than 3.0%, and still more preferably less than 1.0%. In addition, by setting the content of the BaO component to 25.0% or less, the desired refractive index can also be easily obtained, and devitrification caused by excessive inclusion of these components can be reduced. Therefore, the content of the BaO component is preferably 25.0% or less, more preferably less than 20.0%, and still more preferably less than 15.0%. MgO component, CaO component, SrO component and BaO component can use MgCO 3 , MgF 2 , CaCO 3 , CaF 2 , Sr(NO 3 ) 2 , SrF 2 , BaCO 3 , Ba(NO 3 ) 2 , BaF 2 etc. as raw materials . When the content of Li 2 O, Na 2 O, and K 2 O exceeds 0%, it is an optional component that can improve the meltability of the glass and reduce the glass transition point. On the other hand, by setting each of the Li 2 O component, Na 2 O component, and K 2 O component to 10.0% or less, the refractive index of the glass can be prevented from falling, and the devitrification of the glass can be reduced. In addition, in particular, the content of the Li 2 O component is reduced, thereby increasing the viscosity of the glass, thereby reducing the texture of the glass. Therefore, the content of the Li 2 O component, the Na 2 O component, and the K 2 O component are each preferably 10.0% or less, more preferably less than 5.0%, still more preferably less than 3.0%, and still more preferably less than 1.0 %, more preferably less than 0.5%, and still more preferably less than 0.1%. Li 2 O component, Na 2 O component and K 2 O component can use Li 2 CO 3 , LiNO 3 , Li 2 CO 3 , Na 2 CO 3 , NaNO 3 , NaF, Na 2 SiF 6 , K 2 CO 3 , KNO 3. KF, KHF 2 , K 2 SiF 6 and the like are used as raw materials. When the P 2 O 5 component contains more than 0%, it is an optional component that reduces the liquidus temperature of the glass and improves the resistance to devitrification. On the other hand, by setting the content of the P 2 O 5 component to 10.0% or less, the chemical durability of the glass, especially the decrease in water resistance, is suppressed. Therefore, the content of the P 2 O 5 component is preferably 10.0% or less, more preferably less than 5.0%, and still more preferably less than 3.0%. For the P 2 O 5 component, Al(PO 3 ) 3 , Ca(PO 3 ) 2 , Ba(PO 3 ) 2 , BPO 4 , H 3 PO 4 and the like can be used as raw materials. When the GeO 2 component contains more than 0%, it is an optional component that can increase the refractive index of the glass and improve the resistance to devitrification. However, since GeO 2 has a high raw material price, if the content of GeO 2 is large, the production cost becomes high. Therefore, the effect of reducing the Gd 2 O 3 component or the Ta 2 O 5 component is canceled. Therefore, the content of the GeO 2 component is preferably 10.0% or less, more preferably less than 5.0%, still more preferably less than 3.0%, still more preferably less than 1.0%, and still more preferably less than 0.1%. In particular, from the viewpoint of reducing the material cost, the GeO 2 component may not be included. As the GeO 2 component, GeO 2 or the like can be used as a raw material. When the Al 2 O 3 component and the Ga 2 O 3 component contain more than 0%, it is an optional component that can improve the chemical durability of the glass and can improve the devitrification resistance of the molten glass. On the other hand, by setting the content of each of the Al 2 O 3 component and the Ga 2 O 3 component to 15.0% or less, the liquidus temperature of the glass is lowered and the devitrification resistance is improved. Therefore, the content of each of the Al 2 O 3 component and the Ga 2 O 3 component is preferably 15.0% or less, more preferably less than 10.0%, still more preferably less than 5.0%, and still more preferably less than 3.0% . For the Al 2 O 3 component and the Ga 2 O 3 component, Al 2 O 3 , Al(OH) 3 , AlF 3 , Ga 2 O 3 , Ga(OH) 3, etc. can be used as raw materials. When the Bi 2 O 3 component contains more than 0%, it is an optional component that increases the refractive index and reduces the glass transition point. On the other hand, by setting the content of the Bi 2 O 3 component to 15.0% or less, the liquidus temperature of the glass is lowered and the devitrification resistance is improved. Therefore, the content of the Bi 2 O 3 component is preferably 15.0% or less, more preferably less than 10.0%, still more preferably less than 5.0%, still more preferably less than 3.0%, and still more preferably less than 1.0% . For the Bi 2 O 3 component, Bi 2 O 3 or the like can be used as a raw material. When the TeO 2 component contains more than 0%, it is an optional component that increases the refractive index and reduces the glass transition point. On the other hand, TeO 2 has a problem of alloying with platinum when melting glass raw materials with a crucible made of platinum or a melting tank formed of platinum with a part in contact with molten glass. Therefore, the content of the TeO 2 component is preferably 15.0% or less, more preferably less than 10.0%, still more preferably less than 5.0%, still more preferably less than 3.0%, and still more preferably less than 1.0%. For the TeO 2 component, TeO 2 or the like can be used as a raw material. When the SnO 2 component contains more than 0%, it is an optional component that reduces the oxidation and clarification of the molten glass, and improves the visible light transmittance of the glass. On the other hand, by setting the content of the SnO 2 component to 3.0% or less, the coloring of the glass due to the reduction of the molten glass or the devitrification of the glass can be reduced. In addition, since the alloying between the SnO 2 component and the melting equipment (especially noble metals such as Pt) is reduced, the life of the melting equipment is extended. Therefore, the content of the SnO 2 component is preferably 3.0% or less, more preferably less than 1.0%, still more preferably less than 0.5%, and still more preferably less than 0.1%. For the SnO 2 component, SnO, SnO 2 , SnF 2 , SnF 4, etc. can be used as a raw material. When the Sb 2 O 3 component contains more than 0%, it is an optional component that can defoam molten glass. On the other hand, if the amount of Sb 2 O 3 is too large, the transmittance in the short wavelength region of the visible light region deteriorates. Therefore, the content of the Sb 2 O 3 component is preferably 1.0% or less, more preferably less than 0.5%, and still more preferably less than 0.3%. Sb 2 O 3 ingredients may be employed Sb 2 O 3, Sb 2 O 5, Na 2 H 2 Sb 2 O 7 · 5H 2 O and the like as a raw material. In addition, the component for clarifying and defoaming glass is not limited to the above-mentioned Sb 2 O 3 component, and a clarifying agent, a defoaming agent, or a combination thereof known in the glass manufacturing field can be used. When the F component contains more than 0%, it is an optional component that can increase the Abbe number of the glass, reduce the glass transition point, and improve the resistance to devitrification. However, if the content of the F component, that is, the total amount of F as part or all of the fluoride substituted with one or more of the above-mentioned metal element oxides, exceeds 15.0%, the F component volatilizes As the amount increases, it is not easy to obtain stable optical constants, and it is difficult to obtain homogeneous glass. Also, the Abbe number has increased excessively. Therefore, the content of the F component is preferably 15.0% or less, more preferably less than 10.0%, still more preferably less than 5.0%, and still more preferably less than 3.0%. The F component can be contained in the glass by using, for example, ZrF 4 , AlF 3 , NaF, CaF 2 and the like as a raw material. The ratio (molar ratio) of the content of the SiO 2 component to the content of the B 2 O 3 component is preferably 0.13 or more and 1.70 or less. In particular, by setting the molar ratio to 0.13 or more, it is possible to easily obtain a stable glass that reduces devitrification and is resistant to mass production. Therefore, the molar ratio SiO 2 /B 2 O 3 is preferably 0.13 or more, more preferably 0.15 or more, still more preferably 0.17 or more, still more preferably 0.18 or more, still more preferably more than 0.20, still more preferably more than 0.24, more preferably more than 0.28, still more preferably more than 0.32. On the other hand, by setting the molar ratio to 1.70 or less, the rise of the glass transition point is suppressed. Therefore, the molar ratio SiO 2 /B 2 O 3 is preferably 1.70 or less, more preferably 1.50 or less, still more preferably 1.30 or less, still more preferably less than 1.30, still more preferably less than 1.20, and still more preferably It is less than 1.00, more preferably less than 0.85, still more preferably less than 0.80, and still more preferably less than 0.70. The total amount (molar sum) of the Ta 2 O 5 component, the Nb 2 O 5 component, the WO 3 component, the Gd 2 O 3 component, and the Yb 2 O 3 component is preferably less than 10.0%. Thereby, since the content of these expensive components is reduced, the material cost of the glass can be suppressed. Therefore, Mole and Ta 2 O 5 +Nb 2 O 5 +WO 3 +Gd 2 O 3 +Yb 2 O 3 are preferably up to 10.0%, more preferably less than 8.0%, and still more preferably less than 5.0 %, more preferably less than 3.0%, still more preferably less than 2.0%, still more preferably less than 1.0%. Especially from the viewpoint of obtaining glass with low material cost, it is more preferable to set Mole and Ta 2 O 5 +Nb 2 O 5 +WO 3 +Gd 2 O 3 +Yb 2 O 3 to less than 0.1%. The best system is set to 0%. The ratio (molar ratio) of the content of the ZnO component to the content of the La 2 O 3 component and the Y 2 O 3 component is preferably 0.10 or more and 4.00 or less. In particular, by setting the molar ratio to 0.10 or more, the solubility of the glass raw material can be improved, and more stable glass can be easily obtained. Therefore, the molar ratio ZnO/(La 2 O 3 +Y 2 O 3 ) is preferably 0.10, more preferably 0.15, still more preferably 0.20, still more preferably 0.24 as the lower limit, and still more preferably more than 0.26, and further It is more preferably 0.27, even more preferably 0.32, and even more preferably 0.35 as the lower limit. On the other hand, by setting the molar ratio to 4.00 or less, the liquidus temperature can be lowered, and devitrification caused by an excessive drop in the glass transition point can be reduced. Therefore, the molar ratio ZnO/(La 2 O 3 +Y 2 O 3 ) is preferably 4.00, more preferably 3.50, still more preferably 3.00, and even more preferably 2.50 as the upper limit. The total content (mole sum) of Ln 2 O 3 components (where Ln is selected from the group consisting of La, Gd, Y, Yb, and Lu) is preferably 5.0% or more and 40.0% or less . In particular, by setting the sum to 5.0% or more, since the refractive index and Abbe number of glass are improved, it is possible to easily obtain glass having a desired refractive index and Abbe number. Therefore, the molar sum of the Ln 2 O 3 component is preferably 5.0% or more, more preferably more than 8.0%, still more preferably more than 10.0%, still more preferably more than 11.0%, still more preferably more than 12.0%. On the other hand, by setting the sum to 40.0% or less, since the liquidus temperature of the glass becomes lower, the devitrification of the glass can be reduced. In addition, the excessive increase in Abbe number is suppressed. Therefore, the molar sum of the Ln 2 O 3 component is preferably 40.0% or less, more preferably less than 35.0%, still more preferably less than 30.0%, still more preferably less than 27.0%, and still more preferably less than 25.0%, still more preferably less than 22.0%, still more preferably less than 20.0%, still more preferably less than 18.0%, still more preferably less than 16.5%. In particular, in the third optical glass, by containing at least one of the CaO component and the BaO component, even with a smaller content of the Ln 2 O 3 component, the desired high refractive index glass can be obtained, so that the glass can be further reduced. The cost of materials. The total content (molar sum) of the RO component (in the formula, R is selected from one or more selected from the group consisting of Mg, Ca, Sr, and Ba) is preferably 25.0% or less. This suppresses the decrease in refractive index and improves the stability of the glass. Therefore, the molar sum of the RO component is preferably 25.0% or less, more preferably less than 20.0%, and still more preferably less than 15.0%. On the other hand, the molar sum of the RO component is also preferably more than 0%, more preferably more than 1.0%, and still more preferably more than 2.0%. The total content (mole sum) of the Rn 2 O component (in the formula, Rn is one or more selected from the group consisting of Li, Na, and K) is preferably 10.0% or less. Thereby, the viscosity drop of the molten glass can be suppressed, the refractive index of the glass is not easily decreased, and the devitrification of the glass can be reduced. Therefore, the molar sum of the Rn 2 O component is preferably 10.0% or less, more preferably less than 5.0%, still more preferably less than 3.0%, still more preferably less than 1.0%, and still more preferably less than 0.5 %, more preferably less than 0.1%. The total content of RO component (in the formula, R is selected from the group consisting of Mg, Ca, Sr, and Ba) and the total content of ZnO component relative to the Ln 2 O 3 component (in the formula, Ln is selected from La, The ratio (molar ratio) of the total content of one or more of the group consisting of Gd, Y, Yb, and Lu is preferably more than 0.30. Thereby, the material cost of the glass can be further reduced, and the stability of the glass can be improved. Therefore, the molar ratio (RO+ZnO)/Ln 2 O 3 is preferably more than 0.30, more preferably more than 0.45, still more preferably more than 0.50, still more preferably more than 0.80, and still more preferably more than 1.00. On the other hand, from the viewpoint of suppressing the decrease in refractive index, the molar ratio is preferably less than 7.00, more preferably less than 5.00, and still more preferably less than 4.00. The ratio (molar ratio) of the content of the BaO component to the content of the ZnO component is preferably 5.00 or less. Thereby, the meltability of the glass raw material and the stability of the glass are improved. Therefore, the molar ratio of BaO/ZnO is preferably 5.00, more preferably 4.00, still more preferably 3.00, still more preferably 2.80, and still more preferably 2.50 as the upper limit. The ratio (molar ratio) of the content of the BaO component to the total content of the RO component (in the formula, R is one or more selected from the group consisting of Mg, Ca, Sr, and Ba) is preferably 0.50 or more. In this way, the refractive index of the glass is increased. Therefore, the molar ratio BaO/RO is also preferably 0.50, more preferably 0.70, and even more preferably 0.80 as the lower limit. In addition, the upper limit of the molar ratio may be 1.00. <About the components that should not be contained> Next, the components that should not be contained in the optical glass of the present invention and the less desirable components are described. Other ingredients can be added as needed within the scope that does not impair the characteristics of the glass of the invention of this application. But except for Ti, Zr, Nb, W, La, Gd, Y, Yb, Lu, V, Cr, Mn, Fe, Co, Ni, Cu, Ag and Mo and other transition metal components are individually or combined in small amounts When it is contained, it also has the property of coloring the glass and absorbing specific wavelengths in the visible light region. Therefore, especially in optical glass using wavelengths in the visible light region, it is preferably not contained substantially. In addition, lead compounds such as PbO and arsenic compounds such as As 2 O 3 are components that have a high environmental burden, and therefore it is desirable that they are not contained substantially, that is, they are preferably not contained except for unavoidable mixing. In addition, the components of Th, Cd, Tl, Os, Be, and Se have been used as harmful chemical substances in recent years, and have been controlled for use, not only in the manufacturing steps of glass, but also through the processing steps and the processing after productization. Previously, environmental countermeasures must be taken. Therefore, in the case of emphasizing environmental impact, it is better not to contain them in substance. [Manufacturing method] The optical glass of the present invention is manufactured in the following manner, for example. That is, the above-mentioned raw materials are uniformly mixed in such a way that each component is within a specific content range, and the resulting mixture is put into a platinum crucible, and the glass raw material is melted in an electric furnace at a temperature range of 1100 to 1500 ℃ for 2 to 5 hours according to the melting difficulty of the glass material. After mixing and homogenizing, it is lowered to an appropriate temperature, and then poured into the mold, and slowly cooled to make it. In this case, it is preferable to use one with high melting property as the glass raw material. In this way, since it can be melted at a lower temperature or in a shorter time, the productivity of the glass can be improved and the production cost can be reduced. In addition, since the volatilization of the components or the reaction with the crucible is reduced, it is easy to obtain glass with less coloration. [Physical Properties] The optical glass of the present invention preferably has a high refractive index and a high Abbe number (low dispersion). The refractive index (n d ) of the optical glass of the present invention is preferably 1.70, more preferably 1.72, still more preferably 1.74, still more preferably 1.75, still more preferably 1.78, and even more preferably 1.80 as the lower limit. In particular, the refractive index (n d ) of the first optical glass is also preferably 1.75, more preferably 1.78, still more preferably 1.79, and even more preferably 1.80 as the lower limit. On the other hand, the refractive index (n d ) is also preferably 2.10, more preferably 2.00, still more preferably 1.90, and even more preferably 1.85 as the upper limit. In particular, the refractive index (n d ) of the second optical glass is also preferably 1.90, more preferably 1.88, and even more preferably 1.85 as the upper limit. The Abbe number (ν d ) of the optical glass of the present invention is preferably 25, more preferably 27, still more preferably 28, still more preferably 30, and even more preferably 32 as the lower limit. On the other hand, the Abbe number (ν d ) is preferably 50, more preferably 48, still more preferably 45, still more preferably 43, still more preferably 42, still more preferably 41, and still more preferably 40.5 is the upper limit. In particular, the Abbe number (ν d ) of the first optical glass is also preferably 48, more preferably 45, still more preferably 43, and even more preferably 41 as the upper limit. By having such a high refractive index, even if the optical element is thinned, a large amount of light refraction can be obtained. In addition, by having such low dispersion, when used as a single lens, the focus shift (chromatic aberration) caused by the wavelength of light can be reduced. Therefore, for example, when an optical system is combined with an optical element having high dispersion (low Abbe number) to form an optical system, it is possible to reduce aberrations and achieve high imaging characteristics as the entire optical system. In this way, the optical glass of the present invention is useful in optical design, especially when constructing an optical system, it can achieve high imaging characteristics, etc., and achieve miniaturization of the optical system, and expand the degree of freedom of optical design. The optical glass of the present invention preferably has high devitrification resistance, and specifically has a low liquidus temperature. That is, the liquidus temperature of the optical glass of the present invention is preferably 1200°C, more preferably 1150°C, and even more preferably 1100°C as the upper limit. As a result, even if the melted glass flows out at a lower temperature, the crystallization of the glass produced is reduced, so the devitrification of the glass when it is formed from the molten state can be reduced, and the optical effects on the optical elements using the glass can be reduced. The impact of characteristics. In addition, since the glass can be formed even if the melting temperature of the glass is lowered, the manufacturing cost of the glass can be reduced by suppressing the energy consumed during glass forming. On the other hand, the lower limit of the liquidus temperature of the optical glass of the present invention is not particularly limited. Most of the liquidus temperature of the glass obtained by the present invention is about 800°C or higher, specifically, 850°C or higher, and more specifically , Above 900 ℃. In addition, the "liquid phase temperature" in this manual refers to a platinum crucible with a capacity of 50 ml. A 30 cc glass cullet is placed in the platinum crucible, heated at 1250 ℃ to a completely molten state, and the temperature is lowered. Keep it at a specific temperature for 1 hour, and immediately observe the glass surface and the presence or absence of crystals in the glass after being taken out of the furnace to cool, the lowest temperature at which crystals are not seen. The specific temperature during cooling here is the temperature of every 10 ℃ between 1200 ℃ and 800 ℃. The optical glass of the present invention preferably has a visible light transmittance, in particular, the transmittance of light on the short-wavelength side of visible light is relatively high, so that there is less coloration. The wavelength (λ 80 ) at which a sample with a thickness of 10 mm in the optical glass of the present invention shows a spectral transmittance of 80% is also preferably 550 nm, more preferably 520 nm, and even more preferably 500 nm as the upper limit. In the optical glass of the present invention, the wavelength (λ 70 ) at which a sample with a thickness of 10 mm shows a spectral transmittance of 70% is also preferably 500 nm, more preferably 450 nm, still more preferably 420 nm, and even more preferably 400 nm Is the upper limit. In the optical glass of the present invention, the shortest wavelength (λ 5 ) at which a sample with a thickness of 10 mm shows a spectral transmittance of 5% is also preferably 400 nm, more preferably 380 nm, and even more preferably 360 nm as the upper limit. By these, the absorption end of the glass is located in the ultraviolet region or its vicinity, and the transparency of the glass to visible light is improved. Therefore, the optical glass can be preferably used for optical elements such as lenses that transmit light. The optical glass of the present invention preferably has a glass transition point (Tg) below 700°C. As a result, the optical glass has a glass transition point below 700 ℃, whereby the glass is softened at a lower temperature, so even if the optical glass is used for press molding, the glass can be easily press-formed at a lower temperature. Therefore, the glass transition point of the optical glass of the present invention is preferably 700°C or lower, more preferably 650°C or lower, and even more preferably 630°C or lower. On the other hand, the glass transition point of optical glass can also be above 500 ℃. Thereby, since the stability of the glass is improved and crystallization is not easily caused, the devitrification during glass production or press forming can be reduced, thereby obtaining glass suitable for press forming. Therefore, the glass transition point of the optical glass of the present invention is also preferably 500°C or higher, more preferably 530°C or higher, and even more preferably 550°C or higher. The optical glass of the present invention preferably has a yield point (At) below 800°C. The yield point is one of the indexes indicating the softness of the glass similarly to the glass transition point, and it is an index indicating the temperature close to the press forming temperature. Therefore, by using glass with a yield point of 800 ℃ or less, even if optical glass is used for press forming, the glass can be easily press-formed at a lower temperature. Therefore, the yield point of the optical glass of the present invention is preferably 800°C, more preferably 750°C, and even more preferably 700°C as the upper limit. In addition, the yield point of the optical glass of the present invention is not particularly limited. It is also preferably 500°C, more preferably 550°C, and even more preferably 600°C as the lower limit. The optical glass of the present invention preferably has a smaller specific gravity. More specifically, the specific gravity of the optical glass of the present invention is 5.00 or less. As a result, the quality of the optical element or the optical machine using it is reduced, which contributes to the lighter weight of the optical machine. Therefore, the specific gravity of the optical glass of the present invention is preferably 5.00, more preferably 4.70, and even more preferably 4.50 as the upper limit. In addition, the specific gravity of the optical glass of the present invention is often about 3.00 or more, more specifically, 3.30 or more, and still more specifically, 3.50 or more. The specific gravity of the optical glass of the present invention is measured based on the Japan Optical Glass Industry Association standard JOGIS05-1975 "Method for Measuring the Specific Gravity of Optical Glass". The optical glass of the present invention preferably has a smaller average linear expansion coefficient (α). In particular, the average linear expansion coefficient of the optical glass of the present invention is preferably 100×10 -7 K -1 , more preferably 9×10 -7 K -1 , and even more preferably 80×10 -7 K -1 as the upper limit . Thereby, when the optical glass is press-formed by the forming mold, the total amount of expansion or contraction caused by the temperature change of the glass is reduced. Therefore, it is difficult to break the optical glass during press forming, and the productivity of the optical element can be improved. [Pre-formed material and optical element] A glass molded body can be made from the manufactured optical glass using methods such as grinding, or hot press molding or precision press molding. That is, the optical glass can be machined by grinding and polishing to produce a glass molded body, or a preform for mold press molding can be produced from the optical glass, and the preform can be reheated and pressed and then polished. A glass molded body is produced, or a preform made by grinding or a preform formed by a well-known float forming or the like is precision press-formed to produce a glass molded body. In addition, the method of manufacturing a glass molded object is not limited to these methods. In this way, the optical glass of the present invention can be used in various optical elements and optical designs. Among them, it is particularly preferable to form a pre-formed material from the optical glass of the present invention, and use the pre-formed material to perform hot press forming or precision press forming, etc., to produce optical elements such as lenses or ridges. As a result, it is possible to form a preform with a larger diameter, so that the size of the optical element can be increased, and it can achieve high-definition and high-precision imaging characteristics and projection when used in optical equipment such as cameras or projectors. characteristic. [Examples] Examples of the present invention are shown in Table 1 to Table 26 (No.A1 to No.A73, No.B1 to No.B78, No.C1 to No.C38, No.D1 to No.D6) And the composition of the comparative example (No.X), and the refractive index (n d ), Abbe number (ν d ), glass transition point (Tg), flex point (At), liquidus temperature, and spectroscopy of the glasses The results of wavelengths (λ 5 , λ 70 , λ 80 ), specific gravity and average linear expansion coefficient (α) with transmittance of 5%, 70%, and 80%. Here, the examples (No. A1 to No. A73, No. D1 to No. D6) are mainly examples of the first optical glass. In addition, the examples (No. B1 to No. B78, No. D1 to No. D6) are mainly examples of the second optical glass. In addition, the examples (No. C1 to No. C38) are mainly examples of the third optical glass. In addition, the following examples are for the purpose of illustration after all, and are not limited to these examples. The glasses of the examples and comparative examples of the present invention are all selected equivalent oxides, hydroxides, carbonates, nitrates, fluorides, hydroxides, metaphosphoric acid compounds and other ordinary optical glass of high purity used The raw materials are used as the raw materials of each component, and they are weighed and uniformly mixed according to the composition ratio of each embodiment shown in the table, then put into a platinum crucible, and melt in an electric furnace in the temperature range of 1100-1500 ℃ according to the melting difficulty of the glass raw material 2 After ~5 hours, stir and homogenize, then pour into molds, etc., and slowly cool to make. Here, the refractive index (n d ) and Abbe number (ν d ) of the glass of the examples and comparative examples are measured based on the Japan Optical Glass Industry Association standard JOGIS01-2003. Here, the refractive index (n d ) and the Abbe number (ν d ) are obtained by measuring the glass obtained by setting the slow cooling rate to -25° C./hr. The glass transition point (Tg) and the yield point (At) of the glass of the examples and comparative examples were obtained by measurement using a horizontal expansion measuring device. Here, the sample used for the measurement is φ4.8 mm, the length is 50-55 mm, and the temperature rise rate is set to 4 ℃/min. The transmittance of the glass of the Examples and Comparative Examples was measured based on the Japan Optical Glass Industry Association standard JOGIS02. In addition, in the present invention, by measuring the transmittance of the glass, the presence or absence and degree of coloration of the glass are determined. Specifically, for a parallel polished product with a thickness of 10±0.1 mm, the spectral transmittance of 200 to 800 nm is measured according to JISZ8722, and λ 5 (wavelength at 5% transmittance) and λ 70 (transmittance 70%) are determined. Time wavelength), λ 80 (wavelength at 80% transmittance). The liquidus temperature of the glass of the Examples and Comparative Examples is in a platinum crucible with a capacity of 50 ml. A 30 cc glass cullet-like glass sample is placed in the platinum crucible, heated at 1250 ℃ to a completely molten state, and cooled to Set any temperature every 10°C from 1200°C to 800°C and keep it for 1 hour. After taking it out of the furnace and cooling it, immediately observe the glass surface and whether there are crystals in the glass, and find the lowest temperature at which no crystals are seen. The specific gravity of the glass in the examples and comparative examples was measured based on the Japan Optical Glass Industry Association standard JOGIS05-1975 "Method for Measuring the Specific Gravity of Optical Glass". The average linear expansion coefficient (α) of the glass of the examples and comparative examples is calculated according to the Japan Optical Glass Industry Association standard JOGIS08-2003 "Method for Measuring Thermal Expansion of Optical Glass", and the average linear expansion coefficient at -30～+70 ℃ is calculated. [Table 1]
Figure 105136050-A0304-0001
 [Table 2]
Figure 105136050-A0304-0002
 [table 3]
Figure 105136050-A0304-0003
 [Table 4]
Figure 105136050-A0304-0004
 [table 5]
Figure 105136050-A0304-0005
 [Table 6]
Figure 105136050-A0304-0006
 [Table 7]
Figure 105136050-A0304-0007
 [Table 8]
Figure 105136050-A0304-0008
 [Table 9]
Figure 105136050-A0304-0009
 [Table 10]
Figure 105136050-A0304-0010
 [Table 11]
Figure 105136050-A0304-0011
 [Table 12]
Figure 105136050-A0304-0012
 [Table 13]
Figure 105136050-A0304-0013
 [Table 14]
Figure 105136050-A0304-0014
 [Table 15]
Figure 105136050-A0304-0015
 [Table 16]
Figure 105136050-A0304-0016
 [Table 17]
Figure 105136050-A0304-0017
 [Table 18]
Figure 105136050-A0304-0018
 [Table 19]
Figure 105136050-A0304-0019
 [Table 20]
Figure 105136050-A0304-0020
 [Table 21]
Figure 105136050-A0304-0021
 [Table 22]
Figure 105136050-A0304-0022
 [Table 23]
Figure 105136050-A0304-0023
 [Table 24]
Figure 105136050-A0304-0024
 [Table 25]
Figure 105136050-A0304-0025
 [Table 26]
Figure 105136050-A0304-0026
 As shown in the table, the optical glass of the embodiment of the present invention has a molar and (Nb 2 O 5 +WO 3 ) less than 10.0%, so it can be obtained more cheaply. On the other hand, the glass of the comparative example (No. X) is the glass with Inmol and (Nb 2 O 5 +WO 3 ) at 11.53%, so the material cost is higher. The refractive index (n d ) of the optical glass system of the embodiment of the present invention is all 1.70 or more, and is within the desired range. In particular, the refractive index (n d ) of the optical glass system of the examples (No. A1 to No. A73, No. D1 to No. D6) is 1.75 or more, and more specifically, it is 1.78 or more. In addition, the refractive index (n d ) of the optical glass system of the examples (No. B1 to No. B78) is all 1.74 or more. In addition, the refractive index (n d ) of the optical glass system of the examples (No. C1 to No. C38) is all 1.80 or more. On the other hand, the refractive index (n d ) of the optical glass system in the examples of the present invention is all 2.10 or less. In particular, the refractive index (n d ) of the optical glass system of the examples (No. A1 to No. A73, No. D1 to No. D6) is 2.00 or less. In addition, the refractive index (n d ) of the optical glass system of the Example (No. B1 to No. B78, No. D1 to No. D6) is 1.90 or less. In addition, the refractive index (n d ) of the optical glass system of the examples (No. C1 to No. C38) is all 2.00 or less. The Abbe numbers (ν d ) of the optical glass in the examples of the present invention are all 50 or less, and are within the desired range. In particular, the Abbe numbers (ν d ) of the optical glass systems of the examples (No. A1 to No. A73, No. D1 to No. D6) are all 48 or less, and more specifically, 45 or less. In addition, the Abbe numbers (ν d ) of the optical glass systems of the examples (No. C1 to No. C38) are all 41 or less. On the other hand, the Abbe numbers (ν d ) of the optical glass in the examples of the present invention are all 25 or more, and are within the desired range. In particular, the Abbe numbers (ν d ) of the optical glass systems of the examples (No. A1 to No. A73, No. D1 to No. D6) are all 26 or more. In addition, the Abbe numbers (ν d ) of the optical glass systems of the examples (No. B1 to No. B78, No. D1 to No. D6) are all 30 or more, and more specifically, 32 or more. In addition, the Abbe numbers (ν d ) of the optical glass systems of the examples (No. C1 to No. C38) are all 26 or more. In addition, the optical glass of the present invention forms a stable glass, and is less likely to cause devitrification during glass production. This is presumably because the liquidus temperature of the optical glass of the present invention is 1250°C or lower, more specifically, it is 1210°C or lower. In addition, the optical glass system λ 80 (wavelength at 80% transmittance) of the embodiment of the present invention is all 550 nm or less, more specifically, 490 nm or less. In addition, the optical glass system λ 70 (wavelength at 70% transmittance) of the embodiment of the present invention is all 500 nm or less, more specifically, 490 nm or less. In particular, the optical glass system λ 70 of the examples (No. C1 to No. C38) is all 450 nm or less. In addition, the optical glass system λ 5 (wavelength at 5% transmittance) of the embodiment of the present invention is 400 nm or less, more specifically, 380 nm or less, and is within a desired range. In particular, the optical glass system λ 5 of the examples (No. C1 to No. C38) is all 370 nm or less. Therefore, it can be understood that the refractive index (n d ) and Abbe number (ν d ) of the optical glass of the embodiment of the present invention are within the desired range, and the short-wavelength visible light has high transmittance and high devitrification resistance. In addition, the glass transition point (Tg) of the optical glass system of the embodiment of the present invention is 700°C or less, more specifically, 620°C or less. In addition, the yield point (At) of the optical glass system of the example of the present invention is 800°C or less, more specifically, 670°C or less. Based on these, it can also be inferred that the optical glass system glass of the embodiment of the present invention has a low transition point or a low yield point. In addition, the specific gravity of the optical glass system in the examples of the present invention is all 5.00 or less, more specifically, it is 4.50 or less. In particular, the specific gravity of the optical glass system of the examples of the present invention (No. B1 to No. B78, No. D1 to No. D6) is 4.50 or less. In addition, the average linear expansion coefficient (α) of the optical glass system of the examples is 100×10 -7 K -1 or less, more specifically, 80×10 -7 K -1 or less. Furthermore, the optical glass of the embodiment of the present invention is used to form a glass block, and the glass block is ground and polished to be processed into the shape of a lens and a rim. As a result, it can be processed into stable shapes of various lenses and ridges. Although the purpose of illustration of the present invention has been described in detail above, the present invention is only based on the purpose of illustration. Those skilled in the art should understand that various changes can be made without departing from the spirit and scope of the present invention.

Claims (12)

一種光學玻璃，其以莫耳%計，含有B2O3成分5.0%以上55.0%以下；La2O3成分5.0%以上30.0%以下；ZnO成分為13.27%以上45.0%以下，且莫耳和(Nb2O5+WO3)未達2.0%；莫耳和Ta2O5+Nb2O5+WO3+Gd2O3+Yb2O3未達3.0%；莫耳比SiO2/B2O3為超過0.24且1.70以下；具有1.70以上之折射率(nd)，且具有25以上50以下之阿貝數(νd)。 A kind of optical glass, which contains B 2 O 3 component 5.0% or more and 55.0% or less; La 2 O 3 component is 5.0% or more and 30.0% or less; ZnO component is 13.27% or more and 45.0% or less, and mol and (Nb 2 O 5 +WO 3 ) less than 2.0%; Mohr and Ta 2 O 5 +Nb 2 O 5 +WO 3 +Gd 2 O 3 +Yb 2 O 3 less than 3.0%; Mohr ratio SiO 2 / B 2 O 3 is more than 0.24 and 1.70 or less; has a refractive index (n d ) of 1.70 or more, and an Abbe number (ν d ) of 25 or more and 50 or less. 如請求項1之光學玻璃，其具有1.75以上之折射率(nd)，且具有25以上48以下之阿貝數(νd)。 Such as the optical glass of claim 1, which has a refractive index (n d ) of 1.75 or more, and an Abbe number (ν d ) of 25 or more and 48 or less. 如請求項1之光學玻璃，其具有1.70以上1.90以下之折射率(nd)，且具有30以上50以下之阿貝數(νd)。 Such as the optical glass of claim 1, which has a refractive index (n d ) of 1.70 or more and 1.90 or less, and an Abbe number (ν d ) of 30 or more and 50 or less. 如請求項1之光學玻璃，其中以莫耳%計，含有合計超過0%且30.0%以下之CaO成分及BaO成分中至少一者。 Such as the optical glass of claim 1, which contains at least one of the CaO component and the BaO component in a total of more than 0% and 30.0% or less in molar %. 如請求項1之光學玻璃，其中以莫耳%計，SiO2成分為0~25.0%；ZrO2成分為0~15.0%。 Such as the optical glass of claim 1, in which the SiO 2 component is 0~25.0% in mole%; the ZrO 2 component is 0~15.0%. 如請求項1之光學玻璃，其中以莫耳%計，Nb2O5成分為0~未達2.0%；WO3成分為0~未達1.0%；Gd2O3成分為0~未達2.0%；Yb2O3成分為0~未達2.0%；Ta2O5成分為0~未達3.0%；TiO2成分為0~未達40.0%；Y2O3成分為0~25.0%；MgO成分為0~10.0%；CaO成分為0~10.0%；SrO成分為0~10.0%；BaO成分為0~25.0%；Li2O成分為0~10.0%；Na2O成分為0~10.0%；K2O成分為0~10.0%；P2O5成分為0~10.0%；GeO2成分為0~10.0%；Al2O3成分為0~15.0%；Ga2O3成分為0~15.0%；Bi2O3成分為0~15.0%；TeO2成分為0~15.0%；SnO2成分為0~3.0%； Sb2O3成分為0~1.0%；作為與上述各金屬元素之1種或2種以上之氧化物之一部分或全部置換而成之氟化物之F之含量為0~15.0莫耳%。 For example, the optical glass of claim 1, in which the Nb 2 O 5 component is 0 to less than 2.0% in mole%; the WO 3 component is 0 to less than 1.0%; the Gd 2 O 3 component is 0 to less than 2.0 %; Yb 2 O 3 composition is 0 to less than 2.0%; Ta 2 O 5 composition is 0 to less than 3.0%; TiO 2 composition is 0 to less than 40.0%; Y 2 O 3 composition is 0 to 25.0%; The composition of MgO is 0~10.0%; the composition of CaO is 0~10.0%; the composition of SrO is 0~10.0%; the composition of BaO is 0~25.0%; the composition of Li 2 O is 0~10.0%; the composition of Na 2 O is 0~10.0 %; K 2 O composition is 0~10.0%; P 2 O 5 composition is 0~10.0%; GeO 2 composition is 0~10.0%; Al 2 O 3 composition is 0~15.0%; Ga 2 O 3 composition is 0 ~15.0%; Bi 2 O 3 composition is 0~15.0%; TeO 2 composition is 0~15.0%; SnO 2 composition is 0~3.0%; Sb 2 O 3 composition is 0~1.0%; as the above-mentioned metal elements The content of F in the fluoride formed by partial or complete replacement of one or more of the oxides is 0~15.0 mol%. 如請求項1之光學玻璃，其中莫耳比ZnO/(La2O3+Y2O3)為0.10以上4.00以下。 Such as the optical glass of claim 1, wherein the molar ratio ZnO/(La 2 O 3 +Y 2 O 3 ) is 0.10 or more and 4.00 or less. 如請求項1之光學玻璃，其中Ln2O3成分(式中，Ln係選自由La、Gd、Y、Yb、Lu所組成之群中之1種以上)之莫耳和為5.0%以上40.0%以下；RO成分(式中，R係選自由Mg、Ca、Sr、Ba所組成之群中之1種以上)之莫耳和為25.0%以下；Rn2O成分(式中，Rn係選自由Li、Na、K所組成之群中之1種以上)之莫耳和為10.0%以下。 Such as the optical glass of claim 1, wherein the molar sum of the Ln 2 O 3 component (where Ln is selected from the group consisting of La, Gd, Y, Yb, and Lu) is 5.0% or more 40.0 % Or less; RO component (where R is selected from one or more of the group consisting of Mg, Ca, Sr, and Ba) has a molar sum of 25.0% or less; Rn 2 O component (where Rn is selected The molar sum of one or more of the group consisting of free Li, Na, and K is 10.0% or less. 如請求項1之光學玻璃，其中莫耳比(RO+ZnO)/Ln2O3超過0.30(式中，R係選自由Mg、Ca、Sr、Ba所組成之群中之1種以上，Ln係選自由La、Gd、Y、Yb、Lu所組成之群中之1種以上)。 Such as the optical glass of claim 1, wherein the molar ratio (RO+ZnO)/Ln 2 O 3 exceeds 0.30 (where R is selected from one or more of the group consisting of Mg, Ca, Sr, and Ba, Ln It is one or more selected from the group consisting of La, Gd, Y, Yb, and Lu). 一種預成形材，其包含如請求項1至9中任一項之光學玻璃。 A preformed material comprising the optical glass according to any one of claims 1 to 9. 一種光學元件，其包含如請求項1至9中任一項之光學玻璃。 An optical element comprising the optical glass according to any one of claims 1 to 9. 一種光學機器，其包含如請求項11之光學元件。 An optical machine comprising the optical element as claimed in claim 11.
TW105136050A 2015-11-06 2016-11-04 Optical glass, preforms and optical components TWI743061B (en)

Applications Claiming Priority (14)

Application Number Priority Date Filing Date Title
JP??2015-218906 2015-11-06
JP2015218904 2015-11-06
JP??2015-218904 2015-11-06
JP??2015-218905 2015-11-06
JP2015218906 2015-11-06
JP2015218905 2015-11-06
JP2016137865A JP6808385B2 (en) 2015-11-06 2016-07-12 Optical glass, preform materials and optical elements
JP??2016-137864 2016-07-12
JP2016137864 2016-07-12
JP??2016-137865 2016-07-12
JP??2016-210892 2016-10-27
JP2016210891A JP6903373B2 (en) 2015-11-06 2016-10-27 Optical glass, preform materials and optical elements
JP??2016-210891 2016-10-27
JP2016210892A JP6866012B2 (en) 2015-11-06 2016-10-27 Optical glass, preform materials and optical elements

Publications (2)

Publication Number Publication Date
TW201731785A TW201731785A (en) 2017-09-16
TWI743061B true TWI743061B (en) 2021-10-21

Family

ID=59444462

Family Applications (1)

Application Number Title Priority Date Filing Date
TW105136050A TWI743061B (en) 2015-11-06 2016-11-04 Optical glass, preforms and optical components

Country Status (2)

Country Link
CN (3) CN117865469A (en)
TW (1) TWI743061B (en)

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP7325927B2 (en) * 2017-12-27 2023-08-15 株式会社オハラ Optical glass, preforms and optical elements
CN110316960B (en) * 2019-07-22 2022-02-11 成都光明光电股份有限公司 Optical glass, glass preform, optical element and optical instrument
EP3915952B1 (en) * 2019-08-26 2022-12-28 AGC Inc. Optical glass

Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS55121925A (en) * 1979-03-14 1980-09-19 Ohara Inc Optical glass
TW200403197A (en) * 2002-06-19 2004-03-01 Schott Glas Lead-free optical glass and the optical element comprising the same
CN1807305A (en) * 2004-11-15 2006-07-26 Hoya株式会社 Optical glass, precision press-molding preform, process for producing the preform, optical element and process for producing the element
CN1840494A (en) * 2005-02-21 2006-10-04 Hoya株式会社 Optical glass, glass gob for press-molding, optical part, process for producing glass shaped material and process for producing optical part
CN101012103A (en) * 2002-12-27 2007-08-08 Hoya株式会社 Optical glass, press-molding glass gob and optical element
TW200804217A (en) * 2006-03-23 2008-01-16 Hoya Corp Optical galss, precision press-molding and process for the production thereof, and optical element and process for the production thereof
CN101271165A (en) * 2007-03-20 2008-09-24 Hoya株式会社 On-vehicle camera lens glass material and on-vehicle camera lens
TW201223907A (en) * 2010-10-08 2012-06-16 Ohara Kk Optical glass, preform material, and optical element
TW201331146A (en) * 2011-12-07 2013-08-01 Ohara Kk Optical glass, preform, and optical element

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS60122749A (en) * 1983-12-02 1985-07-01 Hoya Corp Optical glass
JP3912774B2 (en) * 2002-03-18 2007-05-09 Ｈｏｙａ株式会社 Optical glass for precision press molding, preform for precision press molding and manufacturing method thereof
JP5138401B2 (en) * 2008-01-30 2013-02-06 Ｈｏｙａ株式会社 Optical glass, glass gob for press molding, optical element, manufacturing method thereof, and manufacturing method of optical element blank
CN103459339A (en) * 2011-03-29 2013-12-18 株式会社小原 Optical glass, preform, and optical element
CN104341101A (en) * 2013-07-31 2015-02-11 株式会社小原 Optical glass, preform material and optical element
CN103449720B (en) * 2013-08-22 2016-08-17 成都尤利特光电科技股份有限公司 High refraction, low-dispersion optical glass for mold and manufacture method thereof

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS55121925A (en) * 1979-03-14 1980-09-19 Ohara Inc Optical glass
TW200403197A (en) * 2002-06-19 2004-03-01 Schott Glas Lead-free optical glass and the optical element comprising the same
CN101012103A (en) * 2002-12-27 2007-08-08 Hoya株式会社 Optical glass, press-molding glass gob and optical element
CN1807305A (en) * 2004-11-15 2006-07-26 Hoya株式会社 Optical glass, precision press-molding preform, process for producing the preform, optical element and process for producing the element
CN1840494A (en) * 2005-02-21 2006-10-04 Hoya株式会社 Optical glass, glass gob for press-molding, optical part, process for producing glass shaped material and process for producing optical part
TW200804217A (en) * 2006-03-23 2008-01-16 Hoya Corp Optical galss, precision press-molding and process for the production thereof, and optical element and process for the production thereof
CN101271165A (en) * 2007-03-20 2008-09-24 Hoya株式会社 On-vehicle camera lens glass material and on-vehicle camera lens
TW201223907A (en) * 2010-10-08 2012-06-16 Ohara Kk Optical glass, preform material, and optical element
TW201331146A (en) * 2011-12-07 2013-08-01 Ohara Kk Optical glass, preform, and optical element

Also Published As

Publication number Publication date
TW201731785A (en) 2017-09-16
CN117865468A (en) 2024-04-12
CN117865469A (en) 2024-04-12
CN106927675A (en) 2017-07-07

Similar Documents

Publication Publication Date Title
JP6740422B2 (en) Optical glass and optical element
JP6033486B2 (en) Optical glass, preform material and optical element
TWI616415B (en) Optical glass and optical components
TWI585056B (en) Optical glass and optical components
JP6409039B2 (en) Optical glass and optical element
JP5979723B2 (en) Optical glass and optical element
TWI612019B (en) Optical glass, preforms and optical components
JP6903373B2 (en) Optical glass, preform materials and optical elements
JP6808385B2 (en) Optical glass, preform materials and optical elements
JP5946237B2 (en) Optical glass, preform material and optical element
JP6188553B2 (en) Optical glass, preform material and optical element
JP6363141B2 (en) Optical glass, preform material and optical element
JP5875572B2 (en) Optical glass, preform material and optical element
TWI743061B (en) Optical glass, preforms and optical components
JP6804264B2 (en) Optical glass, preforms and optics
TWI659004B (en) Optical glass, preforms and optical components
JP6866012B2 (en) Optical glass, preform materials and optical elements
JP6062613B2 (en) Optical glass, preform material and optical element
JP6635667B2 (en) Optical glass, lens preform and optical element
JP6689057B2 (en) Optical glass, preforms and optical elements
TWI673245B (en) Optical glass, preforms and optical components
JP6049591B2 (en) Optical glass, preform material and optical element
JP6091251B2 (en) Optical glass and optical element
JP2017057121A (en) Optical glass, preform and optical element
JP6611410B2 (en) Optical glass, preform material and optical element