TWI860239B - Optical glass and optical components - Google Patents
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- 239000005304 optical glass Substances 0.000 title claims abstract description 268
- 230000003287 optical effect Effects 0.000 title claims abstract description 66
- 150000001768 cations Chemical class 0.000 claims abstract description 159
- 239000011521 glass Substances 0.000 claims description 334
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 84
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 70
- 229910021193 La 2 O 3 Inorganic materials 0.000 claims description 44
- 229910018068 Li 2 O Inorganic materials 0.000 claims description 37
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 27
- 229910052760 oxygen Inorganic materials 0.000 claims description 26
- 239000000126 substance Substances 0.000 claims description 26
- 229910015902 Bi 2 O 3 Inorganic materials 0.000 claims description 23
- -1 B 2 O 3 Inorganic materials 0.000 claims description 22
- 229910052792 caesium Inorganic materials 0.000 claims description 10
- 229910052708 sodium Inorganic materials 0.000 claims description 10
- 239000006185 dispersion Substances 0.000 abstract description 115
- 230000007423 decrease Effects 0.000 description 72
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 68
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 66
- ZKATWMILCYLAPD-UHFFFAOYSA-N niobium pentoxide Chemical compound O=[Nb](=O)O[Nb](=O)=O ZKATWMILCYLAPD-UHFFFAOYSA-N 0.000 description 60
- 230000000694 effects Effects 0.000 description 53
- 150000001450 anions Chemical class 0.000 description 34
- 235000012239 silicon dioxide Nutrition 0.000 description 33
- 229910052681 coesite Inorganic materials 0.000 description 32
- 229910052906 cristobalite Inorganic materials 0.000 description 32
- 239000000377 silicon dioxide Substances 0.000 description 32
- 229910052682 stishovite Inorganic materials 0.000 description 32
- 229910052905 tridymite Inorganic materials 0.000 description 32
- CMIHHWBVHJVIGI-UHFFFAOYSA-N gadolinium(III) oxide Inorganic materials [O-2].[O-2].[O-2].[Gd+3].[Gd+3] CMIHHWBVHJVIGI-UHFFFAOYSA-N 0.000 description 26
- 239000000203 mixture Substances 0.000 description 25
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 20
- 230000009477 glass transition Effects 0.000 description 20
- 238000004519 manufacturing process Methods 0.000 description 20
- 238000000034 method Methods 0.000 description 20
- 239000002994 raw material Substances 0.000 description 20
- RUDFQVOCFDJEEF-UHFFFAOYSA-N yttrium(III) oxide Inorganic materials [O-2].[O-2].[O-2].[Y+3].[Y+3] RUDFQVOCFDJEEF-UHFFFAOYSA-N 0.000 description 20
- 238000000465 moulding Methods 0.000 description 18
- 230000005484 gravity Effects 0.000 description 17
- FUJCRWPEOMXPAD-UHFFFAOYSA-N Li2O Inorganic materials [Li+].[Li+].[O-2] FUJCRWPEOMXPAD-UHFFFAOYSA-N 0.000 description 16
- WMWLMWRWZQELOS-UHFFFAOYSA-N bismuth(iii) oxide Chemical compound O=[Bi]O[Bi]=O WMWLMWRWZQELOS-UHFFFAOYSA-N 0.000 description 16
- XUCJHNOBJLKZNU-UHFFFAOYSA-M dilithium;hydroxide Chemical compound [Li+].[Li+].[OH-] XUCJHNOBJLKZNU-UHFFFAOYSA-M 0.000 description 16
- 229910011255 B2O3 Inorganic materials 0.000 description 15
- 230000008859 change Effects 0.000 description 15
- 238000004031 devitrification Methods 0.000 description 15
- MRELNEQAGSRDBK-UHFFFAOYSA-N lanthanum oxide Inorganic materials [O-2].[O-2].[O-2].[La+3].[La+3] MRELNEQAGSRDBK-UHFFFAOYSA-N 0.000 description 15
- 238000002844 melting Methods 0.000 description 15
- 230000008018 melting Effects 0.000 description 15
- KTUFCUMIWABKDW-UHFFFAOYSA-N oxo(oxolanthaniooxy)lanthanum Chemical compound O=[La]O[La]=O KTUFCUMIWABKDW-UHFFFAOYSA-N 0.000 description 15
- YBMRDBCBODYGJE-UHFFFAOYSA-N germanium dioxide Chemical compound O=[Ge]=O YBMRDBCBODYGJE-UHFFFAOYSA-N 0.000 description 14
- 238000002834 transmittance Methods 0.000 description 14
- KKCBUQHMOMHUOY-UHFFFAOYSA-N Na2O Inorganic materials [O-2].[Na+].[Na+] KKCBUQHMOMHUOY-UHFFFAOYSA-N 0.000 description 13
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 12
- 229910052593 corundum Inorganic materials 0.000 description 12
- 239000006060 molten glass Substances 0.000 description 12
- DLYUQMMRRRQYAE-UHFFFAOYSA-N tetraphosphorus decaoxide Chemical compound O1P(O2)(=O)OP3(=O)OP1(=O)OP2(=O)O3 DLYUQMMRRRQYAE-UHFFFAOYSA-N 0.000 description 12
- 229910001845 yogo sapphire Inorganic materials 0.000 description 12
- 230000009467 reduction Effects 0.000 description 11
- 238000000137 annealing Methods 0.000 description 10
- 125000002091 cationic group Chemical group 0.000 description 9
- ADCOVFLJGNWWNZ-UHFFFAOYSA-N antimony trioxide Inorganic materials O=[Sb]O[Sb]=O ADCOVFLJGNWWNZ-UHFFFAOYSA-N 0.000 description 8
- 238000004040 coloring Methods 0.000 description 8
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 description 8
- PBCFLUZVCVVTBY-UHFFFAOYSA-N tantalum pentoxide Inorganic materials O=[Ta](=O)O[Ta](=O)=O PBCFLUZVCVVTBY-UHFFFAOYSA-N 0.000 description 8
- YEAUATLBSVJFOY-UHFFFAOYSA-N tetraantimony hexaoxide Chemical compound O1[Sb](O2)O[Sb]3O[Sb]1O[Sb]2O3 YEAUATLBSVJFOY-UHFFFAOYSA-N 0.000 description 8
- FIXNOXLJNSSSLJ-UHFFFAOYSA-N ytterbium(III) oxide Inorganic materials O=[Yb]O[Yb]=O FIXNOXLJNSSSLJ-UHFFFAOYSA-N 0.000 description 8
- KOPBYBDAPCDYFK-UHFFFAOYSA-N Cs2O Inorganic materials [O-2].[Cs+].[Cs+] KOPBYBDAPCDYFK-UHFFFAOYSA-N 0.000 description 7
- AKUNKIJLSDQFLS-UHFFFAOYSA-M dicesium;hydroxide Chemical compound [OH-].[Cs+].[Cs+] AKUNKIJLSDQFLS-UHFFFAOYSA-M 0.000 description 7
- 230000003595 spectral effect Effects 0.000 description 7
- 229910005793 GeO 2 Inorganic materials 0.000 description 6
- 229910013573 LiO0.5 Inorganic materials 0.000 description 5
- 239000006025 fining agent Substances 0.000 description 5
- CJNBYAVZURUTKZ-UHFFFAOYSA-N hafnium(IV) oxide Inorganic materials O=[Hf]=O CJNBYAVZURUTKZ-UHFFFAOYSA-N 0.000 description 5
- 230000001771 impaired effect Effects 0.000 description 5
- 229910003443 lutetium oxide Inorganic materials 0.000 description 5
- HYXGAEYDKFCVMU-UHFFFAOYSA-N scandium(III) oxide Inorganic materials O=[Sc]O[Sc]=O HYXGAEYDKFCVMU-UHFFFAOYSA-N 0.000 description 5
- 229910016296 BiO1.5 Inorganic materials 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 150000001875 compounds Chemical class 0.000 description 4
- 239000012634 fragment Substances 0.000 description 4
- 238000003384 imaging method Methods 0.000 description 4
- 238000002354 inductively-coupled plasma atomic emission spectroscopy Methods 0.000 description 4
- 229910052697 platinum Inorganic materials 0.000 description 4
- 231100000331 toxic Toxicity 0.000 description 4
- 230000002588 toxic effect Effects 0.000 description 4
- 125000000129 anionic group Chemical group 0.000 description 3
- 239000000470 constituent Substances 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 239000012535 impurity Substances 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 238000003825 pressing Methods 0.000 description 3
- 230000000930 thermomechanical effect Effects 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910052692 Dysprosium Inorganic materials 0.000 description 2
- 229910052691 Erbium Inorganic materials 0.000 description 2
- 229910052693 Europium Inorganic materials 0.000 description 2
- PXGOKWXKJXAPGV-UHFFFAOYSA-N Fluorine Chemical compound FF PXGOKWXKJXAPGV-UHFFFAOYSA-N 0.000 description 2
- 229910052689 Holmium Inorganic materials 0.000 description 2
- 229910052779 Neodymium Inorganic materials 0.000 description 2
- 229910052777 Praseodymium Inorganic materials 0.000 description 2
- 229910052772 Samarium Inorganic materials 0.000 description 2
- 229910003069 TeO2 Inorganic materials 0.000 description 2
- 229910052771 Terbium Inorganic materials 0.000 description 2
- 229910052776 Thorium Inorganic materials 0.000 description 2
- 229910052775 Thulium Inorganic materials 0.000 description 2
- 229910052770 Uranium Inorganic materials 0.000 description 2
- 239000002253 acid Substances 0.000 description 2
- 229910052783 alkali metal Inorganic materials 0.000 description 2
- 150000001340 alkali metals Chemical class 0.000 description 2
- 229910052784 alkaline earth metal Inorganic materials 0.000 description 2
- 150000001342 alkaline earth metals Chemical class 0.000 description 2
- 230000004075 alteration Effects 0.000 description 2
- 229910052785 arsenic Inorganic materials 0.000 description 2
- QVQLCTNNEUAWMS-UHFFFAOYSA-N barium oxide Inorganic materials [Ba]=O QVQLCTNNEUAWMS-UHFFFAOYSA-N 0.000 description 2
- 229910052790 beryllium Inorganic materials 0.000 description 2
- 229910052793 cadmium Inorganic materials 0.000 description 2
- ODINCKMPIJJUCX-UHFFFAOYSA-N calcium oxide Inorganic materials [Ca]=O ODINCKMPIJJUCX-UHFFFAOYSA-N 0.000 description 2
- CETPSERCERDGAM-UHFFFAOYSA-N ceric oxide Chemical compound O=[Ce]=O CETPSERCERDGAM-UHFFFAOYSA-N 0.000 description 2
- 229910000422 cerium(IV) oxide Inorganic materials 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 239000006063 cullet Substances 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 230000002542 deteriorative effect Effects 0.000 description 2
- 229910052731 fluorine Inorganic materials 0.000 description 2
- 239000011737 fluorine Substances 0.000 description 2
- 238000007731 hot pressing Methods 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 125000004435 hydrogen atom Chemical class [H]* 0.000 description 2
- 238000001095 inductively coupled plasma mass spectrometry Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 229910052745 lead Inorganic materials 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 230000005499 meniscus Effects 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 230000001681 protective effect Effects 0.000 description 2
- 230000002285 radioactive effect Effects 0.000 description 2
- 229910052705 radium Inorganic materials 0.000 description 2
- 229910052711 selenium Inorganic materials 0.000 description 2
- 238000003756 stirring Methods 0.000 description 2
- IATRAKWUXMZMIY-UHFFFAOYSA-N strontium oxide Inorganic materials [O-2].[Sr+2] IATRAKWUXMZMIY-UHFFFAOYSA-N 0.000 description 2
- LAJZODKXOMJMPK-UHFFFAOYSA-N tellurium dioxide Chemical compound O=[Te]=O LAJZODKXOMJMPK-UHFFFAOYSA-N 0.000 description 2
- 229910052716 thallium Inorganic materials 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 description 1
- 229910019142 PO4 Inorganic materials 0.000 description 1
- 206010040925 Skin striae Diseases 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 150000004649 carbonic acid derivatives Chemical class 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000005352 clarification Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 150000002222 fluorine compounds Chemical class 0.000 description 1
- 239000005303 fluorophosphate glass Substances 0.000 description 1
- 239000001307 helium Substances 0.000 description 1
- 229910052734 helium Inorganic materials 0.000 description 1
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 150000004679 hydroxides Chemical class 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- CPLXHLVBOLITMK-UHFFFAOYSA-N magnesium oxide Inorganic materials [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 1
- 239000012768 molten material Substances 0.000 description 1
- 150000002823 nitrates Chemical class 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- NBIIXXVUZAFLBC-UHFFFAOYSA-K phosphate Chemical compound [O-]P([O-])([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-K 0.000 description 1
- 239000010452 phosphate Substances 0.000 description 1
- NOTVAPJNGZMVSD-UHFFFAOYSA-N potassium monoxide Inorganic materials [K]O[K] NOTVAPJNGZMVSD-UHFFFAOYSA-N 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 239000010453 quartz Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 230000003685 thermal hair damage Effects 0.000 description 1
- ZNOKGRXACCSDPY-UHFFFAOYSA-N tungsten(VI) oxide Inorganic materials O=[W](=O)=O ZNOKGRXACCSDPY-UHFFFAOYSA-N 0.000 description 1
- XLOMVQKBTHCTTD-UHFFFAOYSA-N zinc oxide Inorganic materials [Zn]=O XLOMVQKBTHCTTD-UHFFFAOYSA-N 0.000 description 1
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
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
本發明提供高折射率/低色散、可用於廣泛的溫度環境的光學玻璃、以及由上述光學玻璃形成的光學元件。上述光學玻璃以陽離子%表示，B 3+的含量與B 3+及Si 4+的合計含量之陽離子比為1/3以上，Ba 2+及Sr 2+的合計含量與Li +、Na +、K +、Cs +、Mg 2+、Ca 2+、Sr 2+及Ba 2+的合計含量之陽離子比為0.62以上，Ba 2+及Li +的合計含量與Na +、K +、Si 4+、Ti 4+、Nb 5+及W 6+的合計含量之陽離子比為8/9以上，Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+及Zr 4+的合計含量為13.00陽離子%以下，La 3+、Y 3+、Ba 2+、Li +的合計含量為36陽離子%以上，Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+、Bi 3+的合計含量與Y 3+的含量之陽離子比為2.0以下。 The present invention provides optical glass with high refractive index and low dispersion, which can be used in a wide range of temperature environments, and an optical element formed of the optical glass. The optical glass is expressed in terms of cation %, and the cation ratio of the content of B 3+ to the total content of B 3+ and Si 4+ is 1/3 or more, the cation ratio of the total content of Ba 2+ and Sr 2+ to the total content of Li + , Na + , K + , Cs + , Mg 2+ , Ca 2+ , Sr 2+ and Ba 2+ is 0.62 or more, the cation ratio of the total content of Ba 2+ and Li + to the total content of Na + , K + , Si 4+ , Ti 4+ , Nb 5+ and W 6+ is 8/9 or more, the total content of Gd 3+ , Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ is 13.00 cation % or less, and the content of La 2+ is 1.25 cation % or less. The total content of Y 3+ , Ba 2+ , and Li + is more than 36 cation %, and the cation ratio of the total content of Gd 3+ , Zn 2+ , Ti 4+ , Nb 5+ , W 6+ , and Bi 3+ to the content of Y 3+ is less than 2.0 .
Description
本發明涉及光學玻璃及光學元件。The present invention relates to optical glass and optical elements.
透鏡、稜鏡這樣的光學元件單獨被使用的情況較少，通常將多個光學元件組合使用。在光學儀器中，用其它構件固定/擔載這些光學元件、或者將這些光學元件黏接/接合而使用。Optical components such as lenses and prisms are rarely used alone, and are usually used in combination. In optical instruments, these optical components are fixed/supported by other components or bonded/joined.
例如，如單眼相機這樣的由人操作的光學儀器放置於室溫環境的情況較多。另一方面，可設想到例如監控攝影機、車載攝影機、搭載於無人機的攝影機等會在更嚴苛的高溫或低溫環境中使用。For example, optical instruments operated by humans, such as SLR cameras, are often placed in room temperature environments. On the other hand, it is conceivable that surveillance cameras, car cameras, and cameras mounted on drones are used in more severe high or low temperature environments.
至今為止，對於光學玻璃而言，在溫度範圍100~300℃或20~300℃之比室溫高的溫度環境中的膨脹係數受到關注。然而，如果考慮到上述的實際的使用環境，則需要還關注更低溫範圍中的膨脹係數。Until now, for optical glass, attention has been paid to the expansion coefficient in a temperature range of 100 to 300°C or 20 to 300°C higher than room temperature. However, if the actual use environment described above is taken into consideration, attention should also be paid to the expansion coefficient in a lower temperature range.
一般來說，光學玻璃的-30~70℃下的平均線膨脹係數α L為約1×10 -5℃ -1左右的級別。這是比用於光學儀器的其它構件小的值。因此，在將這樣的光學玻璃作為光學元件用於光學儀器的情況下，光學元件與其它構件的平均線膨脹係數之差變大，存在光學元件的固定、接合因溫度環境而變得不充分之虞。 Generally speaking, the average linear expansion coefficient α L of optical glass at -30~70℃ is about 1×10 -5 ℃ -1 . This is a smaller value than other components used in optical instruments. Therefore, when such optical glass is used as an optical element in an optical instrument, the difference in the average linear expansion coefficient between the optical element and other components becomes large, and there is a risk that the fixation and bonding of the optical element will become insufficient depending on the temperature environment.
另外，在關注如透鏡、稜鏡這樣的光學元件單獨的特性的情況下，玻璃的平均線膨脹係數α L的大小有時也會對光學元件的成像性能造成影響。 例如，在決定相對折射率的溫度係數dn/dT rel.(以下，簡單記載為dn/dT)的因素中，也包括膨脹係數，所述相對折射率的溫度係數是與光學玻璃在相同溫度的空氣中的折射率的溫度係數。因此，相對折射率的溫度係數(dn/dT)的數值也會因玻璃的膨脹係數的變化而變化。 In addition, when focusing on the characteristics of individual optical elements such as lenses and prisms, the size of the average linear expansion coefficient α L of the glass may also affect the imaging performance of the optical element. For example, the expansion coefficient is also included in the factors that determine the temperature coefficient of the relative refractive index dn/dT rel. (hereinafter, simply recorded as dn/dT), which is the temperature coefficient of the refractive index in air at the same temperature as the optical glass. Therefore, the value of the temperature coefficient of the relative refractive index (dn/dT) will also change due to changes in the expansion coefficient of the glass.
作為玻璃的相對折射率的溫度係數(dn/dT)賦予光學元件的成像性能的一例，除了光學元件本身的溫度根據溫度環境、使用條件而變化的光學系統、例如前面所述的監控攝影機、車載攝影機以外，在使用了雷射的光學系統中，在玻璃的相對折射率的溫度係數(dn/dT)大的情況下，由溫度導致的折射率的變化變大，焦距隨著溫度的變化而變化。As an example of the imaging performance that the temperature coefficient of the relative refractive index of glass (dn/dT) imparts to an optical element, in addition to optical systems in which the temperature of the optical element itself changes depending on the temperature environment and usage conditions, such as the surveillance camera and car camera mentioned above, in optical systems using lasers, when the temperature coefficient of the relative refractive index of glass (dn/dT) is large, the change in refractive index caused by temperature becomes larger, and the focal length changes with the change in temperature.
此外，在玻璃的相對折射率的溫度係數(dn/dT)根據溫度而不同的情況下，玻璃的每單位溫度變化時的焦距的偏移量會根據使用溫度而變化。因此，為了進行精密的光學設計，需要在受光元件側調整根據使用溫度而不同的焦距的偏移量，存在裝置的構造複雜化之虞。Furthermore, if the temperature coefficient of the relative refractive index of glass (dn/dT) varies depending on the temperature, the amount of focal length shift per unit temperature change of the glass will vary depending on the operating temperature. Therefore, in order to perform precise optical design, it is necessary to adjust the amount of focal length shift that varies depending on the operating temperature on the light receiving element side, which may complicate the structure of the device.
以往，作為-30~70℃下的平均線膨脹係數α L比較大的玻璃，已知有低折射率/低色散的氟磷酸玻璃、低折射率/高色散的SiO 2-TiO 2/Nb 2O 5系的玻璃。而且，還已知藉由組合由這些玻璃形成的光學元件，能夠補正色差。 Conventionally, as glasses having a relatively large average linear expansion coefficient α L at -30 to 70°C, low refractive index/low dispersion fluorophosphate glass and low refractive index/high dispersion SiO 2 -TiO 2 /Nb 2 O 5 -based glass are known. It is also known that chromatic aberration can be corrected by combining optical elements formed of these glasses.
然而，例如像無人機、車載攝影機那樣，要求盡可能減小光學元件的品質或佔有體積的情況下，光學元件的搭載片數明顯受到限制，無法使用上述那樣的平均線膨脹係數α L比較大的高色散的玻璃。因此，要求使高折射率/低色散的光學元件承擔主要的聚光特性、並藉由低折射/低色散的光學元件將殘存色差去除這樣的光學設計。 However, when the quality or volume of optical components is required to be minimized as in drones and car cameras, the number of optical components mounted is obviously limited, and high-dispersion glass with a relatively large average linear expansion coefficient α L as described above cannot be used. Therefore, an optical design is required in which the high-refractive index/low-dispersion optical component takes on the main light-gathering properties, and the residual chromatic aberration is removed by the low-refractive index/low-dispersion optical component.
高折射率/低色散的光學玻璃是在光學玻璃中比較新的玻璃。在此之前就存在的高折射率/高色散的光學玻璃中，使有助於高折射率的玻璃成分的含量增加來提高折射率。另一方面，在高折射率/低色散的光學玻璃中，藉由增加玻璃的每單位體積的密度、尤其是有助於極化率/折射率的增加的氧的密度，實現了高折射率且低色散化。High refractive index/low dispersion optical glass is a relatively new type of glass among optical glasses. In the high refractive index/high dispersion optical glass that has existed before, the refractive index is increased by increasing the content of glass components that contribute to the high refractive index. On the other hand, in high refractive index/low dispersion optical glass, the density per unit volume of glass is increased, especially the density of oxygen that contributes to the increase of polarizability/refractive index, to achieve high refractive index and low dispersion.
因此，一般來說，高折射率/低色散的光學玻璃的玻璃結構的自由度低，而且具有強固的原子結構，因此，存在平均線膨脹係數α L變小至0.5×10 -5℃~0.7×10 -5℃ -1左右的傾向。也就是說，在光學玻璃中，產生如果要實現高折射率/低色散則平均線膨脹係數α L變得更小這樣的折衷(trade off)選擇的關係，存在難以兼顧高折射率/低色散特性和高平均線膨脹係數α L這樣的問題。 Therefore, in general, the degree of freedom of the glass structure of high refractive index/low dispersion optical glass is low, and it has a strong atomic structure, so there is a tendency for the average linear expansion coefficient α L to be as small as about 0.5×10 -5 ℃ to 0.7×10 -5 ℃ -1 . In other words, in optical glass, there is a trade-off relationship that if high refractive index/low dispersion is to be achieved, the average linear expansion coefficient α L becomes smaller, and there is a problem that it is difficult to take into account both high refractive index/low dispersion characteristics and high average linear expansion coefficient α L.
專利文獻1、2中公開了溫度範圍100~300℃下的平均線膨脹係數，但沒有公開-30~70℃下的平均線膨脹係數α L，也未對平均線膨脹係數α L進行任何研究。 Patent documents 1 and 2 disclose the average linear expansion coefficient in the temperature range of 100 to 300°C, but do not disclose the average linear expansion coefficient α L in the temperature range of -30 to 70°C, nor do they conduct any research on the average linear expansion coefficient α L.
在專利文獻3、4中提出了用於控制玻璃的相對折射率的溫度係數(dn/dT)的技術，但對於控制玻璃的膨脹係數的技術沒有任何公開。另外，也沒有關於控制玻璃的相對折射率的溫度係數(dn/dT)的溫度依賴性的公開。因此，根據專利文獻3、4也難以得到平均線膨脹係數α L高的光學玻璃、以及相對折射率的溫度係數(dn/dT)的溫度依賴性小的光學玻璃。 Patent Documents 3 and 4 propose a technique for controlling the temperature coefficient of the relative refractive index (dn/dT) of glass, but do not disclose any technique for controlling the expansion coefficient of glass. In addition, there is no disclosure regarding the temperature dependence of the temperature coefficient of the relative refractive index (dn/dT) of glass. Therefore, even with Patent Documents 3 and 4, it is difficult to obtain an optical glass having a high average linear expansion coefficient αL and an optical glass having a low temperature dependence of the temperature coefficient of the relative refractive index (dn/dT).
基於這樣的背景，謀求高折射率/低色散、平均線膨脹係數α L比較大、能夠用於廣泛的溫度環境的光學玻璃。 [現有技術文獻] [專利文獻] Against this background, there is a need for optical glass with high refractive index/low dispersion, relatively large average linear expansion coefficient α L , and capable of being used in a wide range of temperature environments. [Prior Art Literature] [Patent Literature]
專利文獻1：中國專利申請公開第110590155號公報 專利文獻2：中國專利申請公開第110963702號公報 專利文獻3：日本特開第2019-11232號公報 專利文獻4：日本特開第2018-203605號公報 Patent document 1: China Patent Application Publication No. 110590155 Patent document 2: China Patent Application Publication No. 110963702 Patent document 3: Japanese Patent Publication No. 2019-11232 Patent document 4: Japanese Patent Publication No. 2018-203605
[發明要解決的問題][Problem the invention is intended to solve]
因此，本發明的目的在於，提供高折射率/低色散、能夠用於廣泛的溫度環境的光學玻璃、以及包含上述光學玻璃的光學元件。 [用以解決問題的手段] Therefore, an object of the present invention is to provide optical glass having a high refractive index and low dispersion and capable of being used in a wide range of temperature environments, and an optical element comprising the optical glass. [Means for solving the problem]
本發明人等發現，藉由玻璃組成的調整，即使是高折射率/低色散也能夠將平均線膨脹係數α L控制為一定的大小以上，從而完成了本發明。 The inventors of the present invention have discovered that by adjusting the glass composition, the average linear expansion coefficient α L can be controlled to be above a certain level even with a high refractive index/low dispersion, thereby completing the present invention.
本發明的主旨如下所述。 (1) 一種光學玻璃，其中，以陽離子%表示， B 3+的含量與B 3+及Si 4+的合計含量的陽離子比[B 3+/(B 3++Si 4+)]為1/3以上， Ba 2+及Sr 2+的合計含量與Li +、Na +、K +、Cs +、Mg 2+、Ca 2+、Sr 2+及Ba 2+的合計含量的陽離子比[(Ba 2++Sr 2+)/(Li ++Na ++K ++Cs ++Mg 2++Ca 2++Sr 2++Ba 2+)]為0.62以上， Ba 2+及Li +的合計含量與Na +、K +、Si 4+、Ti 4+、Nb 5+及W 6+的合計含量的陽離子比[(Ba 2++Li +)/(Na ++K ++Si 4++Ti 4++Nb 5++W 6+)]為8/9以上， Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+及Zr 4+的合計含量[Gd 3++Zn 2++Ti 4++Nb 5++W 6++Zr 4+]為13.00陽離子%以下， La 3+、Y 3+、Ba 2+、Li +的合計含量[La 3++Y 3++Ba 2++Li +]為36陽離子%以上， Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+及Bi 3+的合計含量與Y 3+的含量的陽離子比[(Gd 3++Zn 2++Ti 4++Nb 5++W 6++Bi 3+)/Y 3+]為2.0以下。 The gist of the present invention is as follows. (1) An optical glass, wherein, expressed as cation %, the cation ratio of the content of B 3+ to the total content of B 3+ and Si 4+ [B 3+ /(B 3+ +Si 4+ )] is 1/3 or more, the cation ratio of the total content of Ba 2+ and Sr 2+ to the total content of Li + , Na + , K + , Cs + , Mg 2+ , Ca 2+ , Sr 2+ and Ba 2+ [(Ba 2+ +Sr 2+ )/(Li + +Na + +K + +Cs + +Mg 2+ +Ca 2+ +Sr 2+ +Ba 2+ )] is 0.62 or more, and the total content of Ba 2+ and Li + to the total content of Na + , K + , Si 4+ , Ti 4+ , Nb 5+ and W The cation ratio of the total content of Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ [Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Zr 4+ ] is 8/9 or more, the total content of La 3+ , Y 3+ , Ba 2+ and Li + [La 3+ +Y 3+ +Ba 2+ +Li + ] is 36 cation % or more, the total content of Gd 3+ , Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ [Gd 3+ + Zn 2+ + Ti 4+ + Nb 5+ +W 6+ +Zr 4+ ] is 13.00 cation % or less, the total content of La 3+ , Y 3+ , Ba 2+ and Li + [La 3+ +Y 3+ +Ba 2+ +Li + ] is 36 cation % or more, The cation ratio of the total content of Y 6+ and Bi 3+ to the content of Y 3+ [(Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Bi 3+ )/Y 3+ ] is less than 2.0.
(2) 一種光學玻璃，其中，以陽離子%表示， B 3+的含量與B 3+及Si 4+的合計含量的陽離子比[B 3+/(B 3++Si 4+)]為1/3以上， Ba 2+及Sr 2+的合計含量與Li +、Na +、K +、Cs +、Mg 2+、Ca 2+、Sr 2+及Ba 2+的合計含量的陽離子比[(Ba 2++Sr 2+)/(Li ++Na ++K ++Cs ++Mg 2++Ca 2++Sr 2++Ba 2+)]為0.62以上， Ba 2+及Li +的合計含量與Na +、K +、Si 4+、Ti 4+、Nb 5+及W 6+的合計含量的陽離子比[(Ba 2++Li +)/(Na ++K ++Si 4++Ti 4++Nb 5++W 6+)]為8/9以上， Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+及Zr 4+的合計含量[Gd 3++Zn 2++Ti 4++Nb 5++W 6++Zr 4+]為13.00陽離子%以下， La 3+、Y 3+、Ba 2+、Li +的合計含量[La 3++Y 3++Ba 2++Li +]為36陽離子%以上， La 3+、Gd 3+及Y 3+的合計含量與B 3+的含量、Si 4+的含量的2倍、Al 3+的含量的合計的陽離子比[(La 3++Gd 3++Y 3+)/{B 3++(2×Si 4+)+Al 3+}]為0.360以上。 (2) An optical glass, wherein, expressed as cation %, the cation ratio of the content of B 3+ to the total content of B 3+ and Si 4+ [B 3+ /(B 3+ +Si 4+ )] is 1/3 or more, the cation ratio of the total content of Ba 2+ and Sr 2+ to the total content of Li + , Na + , K + , Cs + , Mg 2+ , Ca 2+ , Sr 2+ and Ba 2+ [(Ba 2+ +Sr 2+ )/(Li + +Na + +K + +Cs + +Mg 2+ +Ca 2+ +Sr 2+ +Ba 2+ )] is 0.62 or more, and the total content of Ba 2+ and Li + to the total content of Na + , K + , Si 4+ , Ti 4+ , Nb 5+ and W The cation ratio of the total content of Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ [(Ba 2+ +Li + )/(Na + +K + +Si 4+ +Ti 4+ +Nb 5+ +W 6+ )] is 8/9 or more, the total content of Gd 3+ , Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ [Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Zr 4+ ] is 13.00 cation % or less, the total content of La 3+ , Y 3+ , Ba 2+ and Li + [La 3+ +Y 3+ +Ba 2+ +Li + ] is 36 cation % or more, the total content of La 3+ , Gd 3+ and Y 3+ and the content of B 3+ , Si 4+ are 2.5 cation % or less, and the total content of Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ are 2.5 cation % or less. The total cation ratio of twice the content of Si 4+ and the content of Al 3+ [(La 3+ +Gd 3+ +Y 3+ )/{B 3+ +(2×Si 4+ )+Al 3+ }] is 0.360 or more.
(3) 一種光學玻璃，其中，以氧化物基準計，將玻璃成分SiO 2、B 2O 3、Al 2O 3、Li 2O、Na 2O、K 2O、Cs 2O、MgO、CaO、SrO、BaO、ZnO、La 2O 3、Gd 2O 3、Y 2O 3、ZrO 2、TiO 2、Nb 2O 5、WO 3及Bi 2O 3的以質量%表示的含量分別設為C(SiO 2)、C(B 2O 3)、C(Al 2O 3)、C(Li 2O)、C(Na 2O)、C(K 2O)、C(Cs 2O)、C(MgO)、C(CaO)、C(SrO)、C(BaO)、C(ZnO)、C(La 2O 3)、C(Gd 2O 3)、C(Y 2O 3)、C(ZrO 2)、C(TiO 2)、C(Nb 2O 5)、C(WO 3)及C(Bi 2O 3)， 將SiO 2、BO 1.5、AlO 1.5、LiO 0.5、NaO 0.5、KO 0.5、CsO 0.5、MgO、CaO、SrO、BaO、ZnO、LaO 1.5、GdO 1.5、YO 1.5、ZrO 2、TiO 2、NbO 2.5、WO 3及BiO 1.5的各化學式量分別設為M(SiO 2)、M(BO 1.5)、M(AlO 1.5)、M(LiO 0.5)、M(NaO 0.5)、M(KO 0.5)、M(CsO 0.5)、M(MgO)、M(CaO)、M(SrO)、M(BaO)、M(ZnO)、M(LaO 1.5)、M(GdO 1.5)、M(YO 1.5)、M(ZrO 2)、M(TiO 2)、M(NbO 2.5)、M(WO 3)及M(BiO 1.5)， 並且設定： A1＝{C(B 2O 3)/M(BO 1.5)}/{C(B 2O 3)/M(BO 1.5)+C(SiO 2)/M(SiO 2)}、 B1＝{C(BaO)/M(BaO)+C(SrO)/M(SrO)}/{C(Li 2O)/M(LiO 0.5)+C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(Cs 2O)/M(CsO 0.5)+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}、 C1＝{C(BaO)/M(BaO)+C(Li 2O)/M(LiO 0.5)}/{C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(SiO 2)/M(SiO 2)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)}、 D1＝C(Gd 2O 3)+C(ZnO)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)+C(ZrO 2)、 E1＝{C(La 2O 3)+C(Gd 2O 3)+C(Y 2O 3)}/{C(SiO 2)+C(B 2O 3)+C(Al 2O 3)}、 F1＝{C(Gd 2O 3)/M(GdO 1.5)+C(ZnO)/M(ZnO)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)+C(Bi 2O 3)/M(BiO 1.5)}/{C(Y 2O 3)/M(YO 1.5)}時， A1為1/3以上， B1為0.62以上， C1為8/9以上， D1為13.50以下， E1為1.25以上， F1為2.0以下。 (3) An optical glass, wherein the contents of glass components SiO 2 , B 2 O 3 , Al 2 O 3 , Li 2 O, Na 2 O, K 2 O, Cs 2 O, MgO, CaO, SrO, BaO, ZnO, La 2 O 3 , Gd 2 O 3 , Y 2 O 3 , ZrO 2 , TiO 2 , Nb 2 O 5 , WO 3 and Bi 2 O 3, expressed in mass %, are respectively C(SiO 2 ), C(B 2 O 3 ), C(Al 2 O 3 ), C(Li 2 O), C(Na 2 O), C(K 2 O), C(Cs 2 O), C(MgO), C(CaO), C(SrO), C(BaO), C(ZnO), C(La 2 O 3 ), C(Gd 2 O 3 ), C(Y 2 O 3 ), C(ZrO 2 ), C(TiO 2 ), C(Nb 2 O 5 ), C(WO 3 ) and C(Bi 2 O 3 ), and the chemical formula weights of SiO 2 , BO 1.5 , AlO 1.5 , LiO 0.5 , NaO 0.5 , KO 0.5 , CsO 0.5 , MgO, CaO, SrO, BaO, ZnO, LaO 1.5 , GdO 1.5 , YO 1.5 , ZrO 2 , TiO 2 , NbO 2.5 , WO 3 and BiO 1.5 are respectively designated M(SiO 2 ), M(BO 1.5 ), M(AlO 1.5 ), M(LiO 0.5 ), M(NaO 0.5 ), M(KO 0.5 ), M(CsO 0.5 ), M(MgO), M(CaO), M(SrO), M(BaO), M(ZnO), M(LaO 1.5 ), M(GdO 1.5 ), M(YO 1.5 ), M(ZrO 2 ), M(TiO 2 ), M(NbO 2.5 ) , M(WO 3 ) and M(BiO 1.5 ), and set: A1={C(B 2 O 3 )/M(BO 1.5 )}/{C(B 2 O 3 )/M(BO 1.5 )+C(SiO 2 )/M(SiO 2 )}, B1={C(BaO)/M(BaO)+C(SrO)/M(SrO)}/{C(Li 2 O)/M(LiO 0.5 )+C(Na 2 O)/M(NaO 0.5 )+C(K 2 O)/M(KO 0.5 )+C(Cs 2 O)/M(CsO 0.5 )+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}, C1={C(BaO)/M(BaO)+C(Li 2 O)/M(LiO 0.5 )}/{C(Na 2 O)/M(NaO 0.5 )+C(K 2 O)/M(KO 0.5 )+C(SiO 2 )/M(SiO 2 )+C(TiO 2 )/M(TiO 2 )+C(Nb 2 O 5 )/M(NbO 2.5 )+C(WO 3 )/M(WO 3 )}, D1=C(Gd 2 O 3 )+C(ZnO)+C(TiO 2 )+C(Nb 2 O 5 )+C(WO 3 )+C(ZrO 2 ), E1={C(La 2 O 3 )+C(Gd 2 O 3 )+C(Y 2 O 3 )}/{C( SiO 2 )+C(B 2 O 3 )+C(Al 2 O 3 )}, F1={C(Gd 2 O 3 )/M(GdO 1.5 )+C(ZnO)/M(ZnO)+C(TiO 2 )/M(TiO 2 )+C(Nb 2 O 5 )/M(NbO 2.5 )+C(WO 3 )/M(WO 3 )+C(Bi 2 O 3 )/M(BiO 1.5 )}/{C(Y 2 O 3 )/M(YO 1.5 )}, A1 is 1/3 or more, B1 is 0.62 or more, C1 is 8/9 or more, D1 is 13.50 or less, E1 is 1.25 or more, and F1 is 2.0 or less.
(4) 一種光學玻璃，其中，以氧化物基準計，將玻璃成分SiO 2、B 2O 3、Al 2O 3、Li 2O、Na 2O、K 2O、Cs 2O、MgO、CaO、SrO、BaO、ZnO、La 2O 3、Gd 2O 3、Y 2O 3、ZrO 2、TiO 2、Nb 2O 5、WO 3及Bi 2O 3的以質量%表示的含量分別設為C(SiO 2)、C(B 2O 3)、C(Al 2O 3)、C(Li 2O)、C(Na 2O)、C(K 2O)、C(Cs 2O)、C(MgO)、C(CaO)、C(SrO)、C(BaO)、C(ZnO)、C(La 2O 3)、C(Gd 2O 3)、C(Y 2O 3)、C(ZrO 2)、C(TiO 2)、C(Nb 2O 5)、C(WO 3)及C(Bi 2O 3)， 將SiO 2、BO 1.5、AlO 1.5、LiO 0.5、NaO 0.5、KO 0.5、CsO 0.5、MgO、CaO、SrO、BaO、ZnO、LaO 1.5、GdO 1.5、YO 1.5、ZrO 2、TiO 2、NbO 2.5、WO 3及BiO 1.5的各化學式量分別設為M(SiO 2)、M(BO 1.5)、M(AlO 1.5)、M(LiO 0.5)、M(NaO 0.5)、M(KO 0.5)、M(CsO 0.5)、M(MgO)、M(CaO)、M(SrO)、M(BaO)、M(ZnO)、M(LaO 1.5)、M(GdO 1.5)、M(YO 1.5)、M(ZrO 2)、M(TiO 2)、M(NbO 2.5)、M(WO 3)及M(BiO 1.5)， 並且設定： A1＝{C(B 2O 3)/M(BO 1.5)}/{C(B 2O 3)/M(BO 1.5)+C(SiO 2)/M(SiO 2)}、 B1＝{C(BaO)/M(BaO)+C(SrO)/M(SrO)}/{C(Li 2O)/M(LiO 0.5)+C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(Cs 2O)/M(CsO 0.5)+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}、 C1＝{C(BaO)/M(BaO)+C(Li 2O)/M(LiO 0.5)}/{C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(SiO 2)/M(SiO 2)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)}、 D1＝C(Gd 2O 3)+C(ZnO)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)+C(ZrO 2)、 E1＝{C(La 2O 3)+C(Gd 2O 3)+C(Y 2O 3)}/{C(SiO 2)+C(B 2O 3)+C(Al 2O 3)}、 G1＝C(BaO)/M(BaO)+C(La 2O 3)/M(LaO 1.5)+C(Li 2O)/M(LiO 0.5)+C(Y 2O 3)/M(YO 1.5)時， A1為1/3以上， B1為0.62以上， C1為8/9以上， D1為13.50以下， E1為1.25以上， G1為0.47以上。 (4) An optical glass, wherein the contents of glass components SiO 2 , B 2 O 3 , Al 2 O 3 , Li 2 O, Na 2 O, K 2 O, Cs 2 O, MgO, CaO, SrO, BaO, ZnO, La 2 O 3 , Gd 2 O 3 , Y 2 O 3 , ZrO 2 , TiO 2 , Nb 2 O 5 , WO 3 and Bi 2 O 3, expressed in mass %, are respectively C(SiO 2 ), C(B 2 O 3 ), C(Al 2 O 3 ), C(Li 2 O), C(Na 2 O), C(K 2 O), C(Cs 2 O), C(MgO), C(CaO), C(SrO), C(BaO), C(ZnO), C(La 2 O 3 ), C(Gd 2 O 3 ), C(Y 2 O 3 ), C(ZrO 2 ), C(TiO 2 ), C(Nb 2 O 5 ), C(WO 3 ) and C(Bi 2 O 3 ), and the chemical formula weights of SiO 2 , BO 1.5 , AlO 1.5 , LiO 0.5 , NaO 0.5 , KO 0.5 , CsO 0.5 , MgO, CaO, SrO, BaO, ZnO, LaO 1.5 , GdO 1.5 , YO 1.5 , ZrO 2 , TiO 2 , NbO 2.5 , WO 3 and BiO 1.5 are respectively designated M(SiO 2 ), M(BO 1.5 ), M(AlO 1.5 ), M(LiO 0.5 ), M(NaO 0.5 ), M(KO 0.5 ), M(CsO 0.5 ), M(MgO), M(CaO), M(SrO), M(BaO), M(ZnO), M(LaO 1.5 ), M(GdO 1.5 ), M(YO 1.5 ), M(ZrO 2 ), M(TiO 2 ), M(NbO 2.5 ) , M(WO 3 ) and M(BiO 1.5 ), and set: A1={C(B 2 O 3 )/M(BO 1.5 )}/{C(B 2 O 3 )/M(BO 1.5 )+C(SiO 2 )/M(SiO 2 )}, B1={C(BaO)/M(BaO)+C(SrO)/M(SrO)}/{C(Li 2 O)/M(LiO 0.5 )+C(Na 2 O)/M(NaO 0.5 )+C(K 2 O)/M(KO 0.5 )+C(Cs 2 O)/M(CsO 0.5 )+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}, C1={C(BaO)/M(BaO)+C(Li 2 O)/M(LiO 0.5 )}/{C(Na 2 O)/M(NaO 0.5 )+C(K 2 O)/M(KO 0.5 )+C(SiO 2 )/M(SiO 2 )+C(TiO 2 )/M(TiO 2 )+C(Nb 2 O 5 )/M(NbO 2.5 )+C(WO 3 )/M(WO 3 )}, D1=C(Gd 2 O 3 )+C(ZnO)+C(TiO 2 )+C(Nb 2 O 5 )+C(WO 3 )+C(ZrO 2 ), E1={C(La 2 O 3 )+C(Gd 2 O 3 )+C(Y 2 O 3 )}/{C( SiO 2 )+C(B 2 O 3 )+C(Al 2 O 3 )}, G1=C(BaO)/M(BaO)+C(La 2 O 3 )/M(LaO 1.5 )+C(Li 2 O)/M(LiO 0.5 )+C(Y 2 O 3 )/M(YO 1.5 ), A1 is above 1/3, B1 is above 0.62, C1 is above 8/9, D1 is below 13.50, E1 is above 1.25, and G1 is above 0.47.
(5) 一種光學元件，其包含上述(1)~(4)中任一項所述的光學玻璃。 [發明的效果] (5) An optical element comprising the optical glass described in any one of (1) to (4) above. [Effect of the invention]
根據本發明，能夠提供高折射率/低色散、可用於廣泛的溫度環境的光學玻璃、以及包含上述光學玻璃的光學元件。According to the present invention, it is possible to provide optical glass having a high refractive index and a low dispersion and applicable to a wide range of temperature environments, and an optical element including the optical glass.
以下，對本發明的實施方式進行說明。在第1實施方式及第2實施方式中，基於以陽離子%表示的玻璃組成對本發明的光學玻璃進行說明。因此，在第1、2實施方式中，對於玻璃成分的含量及合計含量而言，只要沒有特別記載，則「%」是指「陽離子%」。The following is an explanation of the embodiments of the present invention. In the first and second embodiments, the optical glass of the present invention is explained based on the glass composition expressed in cation %. Therefore, in the first and second embodiments, for the content and total content of the glass components, "%" means "cation %" unless otherwise specified.
陽離子%是指，將全部陽離子成分的含量的合計設為100%時的莫耳百分率。另外，合計含量是指多種陽離子成分的含量(也包括含量為0%的情況)的合計量。另外，陽離子比是指陽離子%中的陽離子成分彼此的含量(也包括多種陽離子成分的合計含量)的比例(比)。Cationic % refers to the molar percentage when the total content of all cationic components is set to 100%. In addition, the total content refers to the total amount of the contents of multiple cationic components (including the case where the content is 0%). In addition, the cationic ratio refers to the ratio (ratio) of the contents of the cationic components in the cation % (including the total content of multiple cationic components).
需要說明的是，陰離子%是指，將全部陰離子成分的含量的合計設為100%時的莫耳百分率。It should be noted that anion % refers to the molar percentage when the total content of all anionic components is set to 100%.
陽離子成分的價數(例如B 3+的價數為+3，Si 4+的價數為+4，La 3+的價數為+3)是根據習慣而確定的值，以氧化物基準表示作為玻璃成分的B、Si、La時，與表示為B 2O 3、SiO 2、La 2O 3的情況相同。因此，對玻璃組成進行分析時，可以不分析陽離子成分的價數。另外，陰離子成分的價數(例如O 2-的價數為-2)也是根據習慣而確定的值，如上述那樣，與將氧化物基準中的玻璃成分例如表示為B 2O 3、SiO 2、La 2O 3的情況相同。因此，對玻璃組成進行分析時，可以不分析陰離子成分的價數。 The valence of the cationic component (for example, the valence of B 3+ is +3, the valence of Si 4+ is +4, and the valence of La 3+ is +3) is a value determined by convention, and when B, Si, and La as glass components are expressed on an oxide basis, it is the same as when they are expressed as B 2 O 3 , SiO 2 , and La 2 O 3. Therefore, when analyzing the glass composition, the valence of the cationic component does not need to be analyzed. In addition, the valence of the anionic component (for example, the valence of O 2- is -2) is also a value determined by convention, and as described above, it is the same as when the glass components on an oxide basis are expressed as B 2 O 3 , SiO 2 , and La 2 O 3. Therefore, when analyzing the glass composition, the valence of the anionic component does not need to be analyzed.
另外，在第3實施方式及第4實施方式中，基於以質量%表示的玻璃組成對本發明的光學玻璃進行說明。在第3、4實施方式中，只要沒有特別記載，則光學玻璃的玻璃組成以氧化物基準的玻璃組成表示。這裡，「氧化物基準的玻璃組成」是指，藉由換算成玻璃原料在熔融時全部分解而在光學玻璃中以氧化物存在而得到的玻璃組成，各玻璃成分的記載根據習慣而記載為SiO 2、TiO 2等。另外，質量比是指，質量%中的氧化物成分彼此的含量(也包括多種氧化物成分的合計含量)的比例(比)。在第3、4實施方式中，只要沒有特別記載，則玻璃成分的含量及合計含量為質量基準，「%」是指「質量%」。 In the third and fourth embodiments, the optical glass of the present invention is described based on the glass composition expressed in mass %. In the third and fourth embodiments, unless otherwise specified, the glass composition of the optical glass is expressed as a glass composition based on oxides. Here, "glass composition based on oxides" refers to a glass composition obtained by converting glass raw materials into glass that is completely decomposed during melting and exists as oxides in the optical glass, and each glass component is recorded as SiO2 , TiO2 , etc. according to custom. In addition, the mass ratio refers to the ratio (ratio) of the contents of oxide components in mass % (including the total contents of multiple oxide components). In the third and fourth embodiments, unless otherwise specified, the content and total content of the glass components are based on mass, and "%" means "mass %".
玻璃成分的含量可以藉由已知的方法、例如電感耦合電漿原子發射光譜法(ICP-AES)、電感耦合電漿質譜分析法(ICP-MS)等方法來定量。另外，在本說明書及本發明中，構成成分的含量為0%是指實質上不含該構成成分，容許以不可避免的雜質水準包含該成分。The content of the glass component can be quantified by a known method, such as inductively coupled plasma atomic emission spectroscopy (ICP-AES), inductively coupled plasma mass spectrometry (ICP-MS), etc. In addition, in this specification and the present invention, the content of a constituent component of 0% means that the constituent component is not substantially contained, and the inclusion of the constituent component at an unavoidable impurity level is allowed.
在本說明書中，只要沒有特別記載，則折射率是指氦的d線(波長587.56nm)下的折射率nd。In this specification, unless otherwise specified, the refractive index refers to the refractive index nd at the d-line (wavelength 587.56 nm) of helium.
阿貝數νd用作表示與色散相關的性質的值，由以下的式子來表示。其中，nF是在藍色的氫F線(波長486.13nm)下的折射率，nC是在紅色的氫C線(656.27nm)下的折射率。 νd=(nd﹣1)/(nF﹣nC) ・・・(1) The Abbe number νd is used as a value to indicate properties related to dispersion and is expressed by the following formula. nF is the refractive index at the blue hydrogen F line (wavelength 486.13nm), and nC is the refractive index at the red hydrogen C line (656.27nm). νd=(nd﹣1)/(nF﹣nC) ・・・(1)
以下，對第1實施方式~第4實施方式依次詳細地進行說明。The first to fourth embodiments are described in detail below.
第1實施方式 一種光學玻璃，其中，以陽離子%表示， B 3+的含量與B 3+及Si 4+的合計含量的陽離子比[B 3+/(B 3++Si 4+)]為1/3以上， Ba 2+及Sr 2+的合計含量與Li +、Na +、K +、Cs +、Mg 2+、Ca 2+、Sr 2+及Ba 2+的合計含量的陽離子比[(Ba 2++Sr 2+)/(Li ++Na ++K ++Cs ++Mg 2++Ca 2++Sr 2++Ba 2+)]為0.62以上， Ba 2+及Li +的合計含量與Na +、K +、Si 4+、Ti 4+、Nb 5+及W 6+的合計含量的陽離子比[(Ba 2++Li +)/(Na ++K ++Si 4++Ti 4++Nb 5++W 6+)]為8/9以上， Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+及Zr 4+的合計含量[Gd 3++Zn 2++Ti 4++Nb 5++W 6++Zr 4+]為13.00陽離子%以下， La 3+、Y 3+、Ba 2+、Li +的合計含量[La 3++Y 3++Ba 2++Li +]為36陽離子%以上， Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+及Bi 3+的合計含量與Y 3+的含量的陽離子比[(Gd 3++Zn 2++Ti 4++Nb 5++W 6++Bi 3+)/Y 3+]為2.0以下。 A first embodiment of an optical glass, wherein, expressed as cation %, the cation ratio of the content of B 3+ to the total content of B 3+ and Si 4+ [B 3+ /(B 3+ +Si 4+ )] is 1/3 or more, the cation ratio of the total content of Ba 2+ and Sr 2+ to the total content of Li + , Na + , K + , Cs + , Mg 2+ , Ca 2+ , Sr 2+ and Ba 2+ [(Ba 2+ +Sr 2+ )/(Li + +Na + +K + +Cs + +Mg 2+ +Ca 2+ +Sr 2+ +Ba 2+ )] is 0.62 or more, and the total content of Ba 2+ and Li + to the total content of Na + , K + , Si 4+ , Ti 4+ , Nb 5+ and W The cation ratio of the total content of Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ [Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Zr 4+ ] is 8/9 or more, the total content of La 3+ , Y 3+ , Ba 2+ and Li + [La 3+ +Y 3+ +Ba 2+ +Li + ] is 36 cation % or more, the total content of Gd 3+ , Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ [Gd 3+ + Zn 2+ + Ti 4+ + Nb 5+ +W 6+ +Zr 4+ ] is 13.00 cation % or less, the total content of La 3+ , Y 3+ , Ba 2+ and Li + [La 3+ +Y 3+ +Ba 2+ +Li + ] is 36 cation % or more, The cation ratio of the total content of Y 6+ and Bi 3+ to the content of Y 3+ [(Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Bi 3+ )/Y 3+ ] is less than 2.0.
在第1實施方式中，B 3+的含量與B 3+及Si 4+的合計含量的陽離子比[B 3+/(B 3++Si 4+)]為1/3以上。該陽離子比的下限較佳為1.1/3，進一步以1.2/3、1.3/3、1.4/3、1.5/3、1.6/3、1.7/3、1.8/3、1.9/3的順序更佳。另外，該陽離子比的上限較佳為3.0/3，進一步以2.9/3、2.8/3、2.7/3、2.6/3、2.5/3、2.4/3、2.3/3的順序更佳。 In the first embodiment, the cation ratio of the content of B 3+ to the total content of B 3+ and Si 4+ [B 3+ /(B 3+ +Si 4+ )] is 1/3 or more. The lower limit of the cation ratio is preferably 1.1/3, and more preferably in the order of 1.2/3, 1.3/3, 1.4/3, 1.5/3, 1.6/3, 1.7/3, 1.8/3, and 1.9/3. In addition, the upper limit of the cation ratio is preferably 3.0/3, and more preferably in the order of 2.9/3, 2.8/3, 2.7/3, 2.6/3, 2.5/3, 2.4/3, and 2.3/3.
藉由將陽離子比[B 3+/(B 3++Si 4+)]設為上述範圍，能夠得到在-30~70℃的平均線膨脹係數α L大的低色散的光學玻璃。另外，能夠降低玻璃的相對折射率的溫度係數(dn/dT)。此外，即使在大量含有La 3+的情況下，也能夠抑制玻璃的熱穩定性的降低。另一方面，該陽離子比過小時，在大量包含作為提高折射率nd、防止平均線膨脹係數α L的降低的玻璃成分的La 3+及Y 3+的情況下，存在玻璃變得不穩定之虞。另外，該陽離子比過大時，存在玻璃的穩定性、化學耐久性及機械特性降低之虞。 By setting the cation ratio [B 3+ /(B 3+ +Si 4+ )] to the above range, a low-dispersion optical glass having a large average linear expansion coefficient α L at -30 to 70°C can be obtained. In addition, the temperature coefficient (dn/dT) of the relative refractive index of the glass can be reduced. In addition, even when La 3+ is contained in a large amount, the reduction in thermal stability of the glass can be suppressed. On the other hand, when the cation ratio is too small, there is a risk that the glass will become unstable when La 3+ and Y 3+ are contained in large amounts as glass components that increase the refractive index nd and prevent the reduction in the average linear expansion coefficient α L. In addition, when the cation ratio is too large, there is a risk that the stability, chemical durability and mechanical properties of the glass will be reduced.
在第1實施方式中，Ba 2+及Sr 2+的合計含量與Li +、Na +、K +、Cs +、Mg 2+、Ca 2+、Sr 2+及Ba 2+的合計含量的陽離子比[(Ba 2++Sr 2+)/(Li ++Na ++K ++Cs ++Mg 2++Ca 2++Sr 2++Ba 2+)]為0.62以上。該陽離子比的下限較佳為0.63，進一步以0.65、0.67、0.69、0.71、0.73、0.75、0.77、0.79、0.81、0.83、0.85、0.87的順序更佳。另外，該陽離子比的上限較佳為1.00，進一步以0.99、0.98的順序更佳。該陽離子比也可以為1.00。 In the first embodiment, the cation ratio of the total content of Ba2 + and Sr2 + to the total content of Li + , Na + , K + , Cs + , Mg2 + , Ca2 + , Sr2 + and Ba2 + [( Ba2 + + Sr2+ )/(Li + +Na + +K + +Cs + + Mg2 + + Ca2 + + Sr2 + +Ba2 + )] is 0.62 or more. The lower limit of the cation ratio is preferably 0.63, and more preferably in the order of 0.65, 0.67, 0.69, 0.71, 0.73, 0.75, 0.77, 0.79, 0.81, 0.83, 0.85, and 0.87. The upper limit of the cation ratio is preferably 1.00, more preferably in the order of 0.99 and 0.98. The cation ratio may also be 1.00.
藉由將陽離子比[(Ba 2++Sr 2+)/(Li ++Na ++K ++Cs ++Mg 2++Ca 2++Sr 2++Ba 2+)]設為上述範圍，可得到平均線膨脹係數α L大的高折射率的光學玻璃。另外，能夠增大平均線膨脹係數α L，並且抑制熱穩定性的降低。另一方面，該陽離子比過小時，存在平均線膨脹係數α L及折射率nd降低、玻璃的穩定性受損之虞。 By setting the cation ratio [(Ba 2+ +Sr 2+ )/(Li + +Na + +K + +Cs + + Mg 2+ +Ca 2+ +Sr 2+ +Ba 2+ )] within the above range, an optical glass having a large average linear expansion coefficient α L and a high refractive index can be obtained. In addition, the average linear expansion coefficient α L can be increased and a decrease in thermal stability can be suppressed. On the other hand, when the cation ratio is too small, there is a risk that the average linear expansion coefficient α L and the refractive index nd will decrease, and the stability of the glass may be impaired.
在第1實施方式中，Ba 2+及Li +的合計含量與Na +、K +、Si 4+、Ti 4+、Nb 5+及W 6+的合計含量的陽離子比[(Ba 2++Li +)/(Na ++K ++Si 4++Ti 4++Nb 5++W 6+)]為8/9以上。該陽離子比的下限較佳為8.2/9，進一步以8.4/9、8.6/9、8.8/9、9.0/9、9.2/9、9.4/9、9.5/9的順序更佳。另外，該陽離子比的上限較佳為27/9，進一步以25/9、23/9、21/9、19/9、17/9、15/9、13/9、12/9的順序更佳。 In the first embodiment, the cation ratio of the total content of Ba 2+ and Li + to the total content of Na + , K + , Si 4+ , Ti 4+ , Nb 5+ and W 6+ [(Ba 2+ +Li + )/(Na + +K + +Si 4+ +Ti 4+ +Nb 5+ +W 6+ )] is 8/9 or more. The lower limit of the cation ratio is preferably 8.2/9, and more preferably in the order of 8.4/9, 8.6/9, 8.8/9, 9.0/9, 9.2/9, 9.4/9, and 9.5/9. In addition, the upper limit of the cation ratio is preferably 27/9, and more preferably in the order of 25/9, 23/9, 21/9, 19/9, 17/9, 15/9, 13/9, and 12/9.
藉由將陽離子比[(Ba 2++Li +)/(Na ++K ++Si 4++Ti 4++Nb 5++W 6+)]設為上述範圍，可得到平均線膨脹係數α L大的高折射率低色散性的光學玻璃。另外，能夠降低玻璃的相對折射率的溫度係數(dn/dT)。另一方面，該陽離子比過小時，存在平均線膨脹係數α L降低、玻璃的高折射低色散性損失之虞。另外，該陽離子比過大時，存在玻璃的穩定性降低之虞。 By setting the cation ratio [(Ba 2+ +Li + )/(Na + +K + +Si 4+ +Ti 4+ +Nb 5+ +W 6+ )] to the above range, a high refractive index and low dispersion optical glass with a large average linear expansion coefficient α L can be obtained. In addition, the temperature coefficient of the relative refractive index of the glass (dn/dT) can be reduced. On the other hand, when the cation ratio is too small, there is a risk that the average linear expansion coefficient α L is reduced and the high refractive index and low dispersion of the glass are lost. In addition, when the cation ratio is too large, there is a risk that the stability of the glass is reduced.
在第1實施方式中，Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+及Zr 4+的合計含量[Gd 3++Zn 2++Ti 4++Nb 5++W 6++Zr 4+]為13.00%以下。該合計含量的上限較佳為12.50%，進一步以12.00%、11.50%、11.00%、10.50%、10.00%、9.50%、9.00%的順序更佳。另外，該合計含量的下限較佳為0%，進一步以1.00%、2.00%、3.00%、4.00%、5.00%、6.00%、7.00%、8.00%的順序更佳。該合計含量也可以為0%。 In the first embodiment, the total content of Gd 3+ , Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ [Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Zr 4+ ] is 13.00% or less. The upper limit of the total content is preferably 12.50%, and more preferably in the order of 12.00%, 11.50%, 11.00%, 10.50%, 10.00%, 9.50%, and 9.00%. In addition, the lower limit of the total content is preferably 0%, and more preferably in the order of 1.00%, 2.00%, 3.00%, 4.00%, 5.00%, 6.00%, 7.00%, and 8.00%. The total content may also be 0%.
藉由將合計含量[Gd 3++Zn 2++Ti 4++Nb 5++W 6++Zr 4+]設為上述範圍，可藉由抑制平均線膨脹係數α L的降低、並且抑制高色散化而得到高折射率低色散性的光學玻璃。此外，也具有不增大玻璃的相對折射率的溫度係數(dn/dT)的效果。該合計含量可以為0，為了調整阿貝數νd等光學常數，可以將該合計含量設為0。另一方面，該合計含量過大時，存在平均線膨脹係數α L降低、或失去玻璃的高折射低色散性之虞。 By setting the total content [Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Zr 4+ ] to the above range, an optical glass with high refractive index and low dispersion can be obtained by suppressing the decrease of the average linear expansion coefficient α L and suppressing high dispersion. In addition, it also has the effect of not increasing the temperature coefficient (dn/dT) of the relative refractive index of the glass. The total content can be 0, and in order to adjust the optical constants such as the Abbe number νd, the total content can be set to 0. On the other hand, when the total content is too large, there is a risk of reducing the average linear expansion coefficient α L or losing the high refractive index and low dispersion of the glass.
在第1實施方式中，La 3+、Y 3+、Ba 2+、Li +的合計含量[La 3++Y 3++Ba 2++Li +]為36%以上。該合計含量的下限較佳為38%，進一步以40%、41%、42%、43%、44%的順序更佳。另外，該合計含量的上限較佳為55%，進一步以54%、53%、52%、51%、50%、49%、48%、47%的順序更佳。 In the first embodiment, the total content of La 3+ , Y 3+ , Ba 2+ , and Li + [La 3+ +Y 3+ +Ba 2+ +Li + ] is 36% or more. The lower limit of the total content is preferably 38%, and more preferably in the order of 40%, 41%, 42%, 43%, and 44%. In addition, the upper limit of the total content is preferably 55%, and more preferably in the order of 54%, 53%, 52%, 51%, 50%, 49%, 48%, and 47%.
藉由將合計含量[La 3++Y 3++Ba 2++Li +]設為上述範圍，可得到抑制了平均線膨脹係數α L的降低、並且高折射率低色散性的光學玻璃。另外，還具有不增大玻璃的相對折射率的溫度係數(dn/dT)的效果。另一方面，該合計含量過小時，存在平均線膨脹係數α L降低、玻璃的高折射低色散性損失之虞。另外，該合計含量過大時，存在玻璃的熱穩定性降低之虞。 By setting the total content [La 3+ +Y 3+ +Ba 2+ +Li + ] to the above range, an optical glass having a high refractive index and low dispersion while suppressing the decrease in the average linear expansion coefficient α L can be obtained. In addition, there is an effect of not increasing the temperature coefficient of the relative refractive index (dn/dT) of the glass. On the other hand, when the total content is too small, there is a risk that the average linear expansion coefficient α L is reduced and the high refractive index and low dispersion of the glass are lost. In addition, when the total content is too large, there is a risk that the thermal stability of the glass is reduced.
在第1實施方式中，Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+及Bi 3+的合計含量與Y 3+的含量的陽離子比[(Gd 3++Zn 2++Ti 4++Nb 5++W 6++Bi 3+)/Y 3+]為2.0以下。該陽離子比的上限較佳為1.8，進一步以1.6、1.4、1.2、1.1、1.0、0.9、0.8、0.6的順序更佳。另外，該陽離子比的下限較佳為0，進一步以0.1、0.2、0.3、0.4的順序更佳。該陽離子比可以為0。 In the first embodiment, the cation ratio of the total content of Gd 3+ , Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Bi 3+ to the content of Y 3+ [(Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Bi 3+ )/Y 3+ ] is 2.0 or less. The upper limit of the cation ratio is preferably 1.8, and more preferably in the order of 1.6, 1.4, 1.2, 1.1, 1.0, 0.9, 0.8, and 0.6. In addition, the lower limit of the cation ratio is preferably 0, and more preferably in the order of 0.1, 0.2, 0.3, and 0.4. The cation ratio may be 0.
藉由將陽離子比[(Gd 3++Zn 2++Ti 4++Nb 5++W 6++Bi 3+)/Y 3+]設為上述範圍，可得到平均線膨脹係數α L大的光學玻璃。另外，能夠抑制玻璃的熱穩定性的降低。該陽離子比可以為0，為了調整阿貝數νd等光學常數，也可以使該陽離子比大於0。另一方面，該陽離子比過大時，存在平均線膨脹係數α L降低、另外玻璃的高折射低色散性損失之虞。 By setting the cation ratio [(Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Bi 3+ )/Y 3+ ] to the above range, an optical glass having a large average linear expansion coefficient α L can be obtained. In addition, the reduction in the thermal stability of the glass can be suppressed. The cation ratio may be 0, or may be greater than 0 in order to adjust optical constants such as the Abbe number νd. On the other hand, when the cation ratio is too large, there is a risk that the average linear expansion coefficient α L is reduced, and the high refractive index and low dispersion of the glass are lost.
在第1實施方式中，La 3+、Gd 3+及Y 3+的合計含量與B 3+的含量、Si 4+的含量的2倍、Al 3+的含量的合計的陽離子比[(La 3++Gd 3++Y 3+)/{B 3++(2×Si 4+)+Al 3+}]的下限較佳為0.300，進一步可以設為0.333、0.340、或0.350，為了提高高折射率低色散性，也可以設為0.360、0.365、0.370、0.375、0.380、0.390、0.400、0.410、0.420、或0.425。特別地，為了兼顧平均線膨脹係數α L的增大和高折射低色散，上述值的下限較佳為0.440、0.450、0.460、0.470、或0.480。另外，該陽離子比的上限較佳為0.550，進一步以0.540、0.530、0.520、0.510、0.500、0.490的順序更佳。 In the first embodiment, the lower limit of the cation ratio of the total content of La 3+ , Gd 3+ and Y 3+ to the content of B 3+ , twice the content of Si 4+ , and the content of Al 3+ [(La 3+ +Gd 3+ +Y 3+ )/{B 3+ +(2×Si 4+ )+Al 3+ }] is preferably 0.300, and can be further set to 0.333, 0.340, or 0.350. In order to improve the high refractive index and low dispersion properties, it can also be set to 0.360, 0.365, 0.370, 0.375, 0.380, 0.390, 0.400, 0.410, 0.420, or 0.425. In particular, in order to take into account both the increase of the mean linear expansion coefficient α L and the high refractive index and low dispersion, the lower limit of the above value is preferably 0.440, 0.450, 0.460, 0.470, or 0.480. In addition, the upper limit of the cation ratio is preferably 0.550, and further preferably in the order of 0.540, 0.530, 0.520, 0.510, 0.500, and 0.490.
從確保玻璃的穩定性的同時將折射率的降低抑制為最小限度、得到高折射率低色散的光學玻璃的觀點考慮，陽離子比[(La 3++Gd 3++Y 3+)/{B 3++(2×Si 4+)+Al 3+}較佳設為上述範圍。另一方面，該陽離子比過大時，存在玻璃的熱穩定性降低之虞。 From the viewpoint of obtaining a high refractive index and low dispersion optical glass while ensuring the stability of the glass and suppressing the decrease in the refractive index to a minimum, the cation ratio [(La 3+ +Gd 3+ +Y 3+ )/{B 3+ +(2×Si 4+ )+Al 3+ }] is preferably set to the above range. On the other hand, when the cation ratio is too large, there is a possibility that the thermal stability of the glass is reduced.
關於第1實施方式的光學玻璃中的上述以外的玻璃成分的含量及比率，以下示出非限定性的實例。Regarding the contents and ratios of the glass components other than those described above in the optical glass of the first embodiment, non-limiting examples are shown below.
在第1實施方式的光學玻璃中，B 3+及Si 4+的合計含量的下限較佳為30%，進一步以35%、37%、39%、41%、43%的順序更佳。另外，該合計含量的上限較佳為65%，進一步以63%、61%、59%、57%、55%、53%的順序更佳。 In the optical glass of the first embodiment, the lower limit of the total content of B 3+ and Si 4+ is preferably 30%, and more preferably in the order of 35%, 37%, 39%, 41%, and 43%. In addition, the upper limit of the total content is preferably 65%, and more preferably in the order of 63%, 61%, 59%, 57%, 55%, and 53%.
從得到平均線膨脹係數α L大、低色散的光學玻璃的觀點考慮，B 3+及Si 4+的合計含量較佳設為上述範圍。 From the perspective of obtaining an optical glass with a large average linear expansion coefficient α L and low dispersion, the combined content of B 3+ and Si 4+ is preferably set to the above range.
在第1實施方式的光學玻璃中，Ba 2+及Sr 2+的合計含量的下限較佳為10%，進一步以11%、12%、13%、14%、15%、16%、17%、18%、19%的順序更佳。另外，該合計含量的上限較佳為30%，進一步以28%、26%、24%、23%、22%、21%、20%的順序更佳。 In the optical glass of the first embodiment, the lower limit of the total content of Ba 2+ and Sr 2+ is preferably 10%, and more preferably in the order of 11%, 12%, 13%, 14%, 15%, 16%, 17%, 18%, and 19%. In addition, the upper limit of the total content is preferably 30%, and more preferably in the order of 28%, 26%, 24%, 23%, 22%, 21%, and 20%.
從得到平均線膨脹係數α L大、高折射率的光學玻璃的觀點考慮，Ba 2+及Sr 2+的合計含量較佳設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L and a high refractive index, the total content of Ba 2+ and Sr 2+ is preferably set to the above range.
在第1實施方式的光學玻璃中，Li +、Na +、K +、Cs +、Mg 2+、Ca 2+、Sr 2+及Ba 2+的合計含量的合計含量的下限較佳為10%，進一步以11%、12%、13%、14%、15%、16%、17%、18%、19%的順序更佳。另外，該合計含量的上限較佳為30%，進一步以28%、26%、24%、23%、22%、21%、20%的順序更佳。 In the optical glass of the first embodiment, the lower limit of the total content of Li + , Na + , K + , Cs + , Mg 2+ , Ca 2+ , Sr 2+ and Ba 2+ is preferably 10%, and more preferably in the order of 11%, 12%, 13%, 14%, 15%, 16%, 17%, 18%, and 19%. In addition, the upper limit of the total content is preferably 30%, and more preferably in the order of 28%, 26%, 24%, 23%, 22%, 21%, and 20%.
從得到平均線膨脹係數α L大、高折射率的光學玻璃的觀點考慮，Ba 2+及Sr 2+的合計含量較佳設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L and a high refractive index, the total content of Ba 2+ and Sr 2+ is preferably set to the above range.
在第1實施方式的光學玻璃中，Ba 2+及Li +的合計含量的下限較佳為10%，進一步以11%、12%、13%、14%、15%、16%、17%、18%、19%的順序更佳。另外，該合計含量的上限較佳為30%，進一步以28%、26%、24%、23%、22%、21%、20%的順序更佳。 In the optical glass of the first embodiment, the lower limit of the total content of Ba 2+ and Li + is preferably 10%, and more preferably in the order of 11%, 12%, 13%, 14%, 15%, 16%, 17%, 18%, and 19%. In addition, the upper limit of the total content is preferably 30%, and more preferably in the order of 28%, 26%, 24%, 23%, 22%, 21%, and 20%.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點考慮，Ba 2+及Li +的合計含量較佳設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L , a high refractive index and low dispersion, the total content of Ba 2+ and Li + is preferably set to the above range.
在第1實施方式的光學玻璃中，Na +、K +、Si 4+、Ti 4+、Nb 5+及W 6+的合計含量的下限較佳為5%，進一步以6%、7%、8%、9%、10%、11%、12%、13%、14%、15%的順序更佳。另外，該合計含量的上限較佳為30%，進一步以29%、28%、27%、26%、25%、24%、23%、22%、21%、20%、19%的順序更佳。 In the optical glass of the first embodiment, the lower limit of the total content of Na + , K + , Si 4+ , Ti 4+ , Nb 5+ and W 6+ is preferably 5%, and more preferably in the order of 6%, 7%, 8%, 9%, 10%, 11%, 12%, 13%, 14%, and 15%. In addition, the upper limit of the total content is preferably 30%, and more preferably in the order of 29%, 28%, 27%, 26%, 25%, 24%, 23%, 22%, 21%, 20%, and 19%.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點考慮，Na +、K +、Si 4+、Ti 4+、Nb 5+及W 6+的合計含量較佳設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L , a high refractive index and low dispersion, the total content of Na + , K + , Si 4+ , Ti 4+ , Nb 5+ and W 6+ is preferably set to the above range.
在第1實施方式中，Ba 2+的含量與Si 4+、Ti 4+、Nb 5+及W 6+的合計含量的陽離子比[Ba 2+/(Si 4++Ti 4++Nb 5++W 6+)]的下限較佳為0.50，進一步以0.55、0.60、0.65、0.70、0.75、0.80、0.85、0.90、0.95、1.00、1.05的順序更佳。另外，該陽離子比的上限較佳為2.00，進一步以1.95、1.90、1.85、1.80、1.75、1.70、1.65、1.60、1.55、1.50、1.45、1.40、1.35的順序更佳。 In the first embodiment, the lower limit of the cation ratio of Ba 2+ to the combined content of Si 4+ , Ti 4+ , Nb 5+ and W 6+ [Ba 2+ /(Si 4+ +Ti 4+ +Nb 5+ +W 6+ )] is preferably 0.50, and further preferably in the order of 0.55, 0.60, 0.65, 0.70, 0.75, 0.80, 0.85, 0.90, 0.95, 1.00, and 1.05. In addition, the upper limit of the cation ratio is preferably 2.00, and more preferably in the order of 1.95, 1.90, 1.85, 1.80, 1.75, 1.70, 1.65, 1.60, 1.55, 1.50, 1.45, 1.40, and 1.35.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點及減小相對折射率的溫度係數(dn/dT)的觀點考慮，較佳將陽離子比[Ba 2+/(Si 4++Ti 4++Nb 5++W 6+)]設為上述範圍。 From the perspective of obtaining an optical glass with a large average linear expansion coefficient αL , high refractive index and low dispersion, and from the perspective of reducing the temperature coefficient of relative refractive index (dn/dT), it is preferred to set the cation ratio [Ba 2+ /(Si 4+ +Ti 4+ +Nb 5+ +W 6+ )] to the above range.
在第1實施方式中，Ba 2+的含量與Si 4+、B 3+、Ti 4+、Nb 5+及W 6+的合計含量的陽離子比[Ba 2+/(Si 4++B 3++Ti 4++Nb 5++W 6+)]的下限較佳為0.20，進一步以0.22、0.24、0.26、0.28、0.30、0.32、0.34、0.36的順序更佳。另外，該陽離子比的上限較佳為0.60，進一步以0.55、0.50、0.48、0.46、0.44、0.42、0.40、0.38的順序更佳。 In the first embodiment, the lower limit of the cation ratio of the content of Ba 2+ to the total content of Si 4+ , B 3+ , Ti 4+ , Nb 5+ and W 6+ [Ba 2+ /(Si 4+ +B 3+ +Ti 4+ +Nb 5+ +W 6+ )] is preferably 0.20, and more preferably in the order of 0.22, 0.24, 0.26, 0.28, 0.30, 0.32, 0.34, and 0.36. In addition, the upper limit of the cation ratio is preferably 0.60, and more preferably in the order of 0.55, 0.50, 0.48, 0.46, 0.44, 0.42, 0.40, and 0.38.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點及減小相對折射率的溫度係數(dn/dT)的溫度依賴性的觀點考慮，較佳將陽離子比[Ba 2+/(Si 4++B 3++Ti 4++Nb 5++W 6+)]設為上述範圍。 From the perspective of obtaining an optical glass with a large average linear expansion coefficient αL , high refractive index and low dispersion, and from the perspective of reducing the temperature dependence of the temperature coefficient of relative refractive index (dn/dT), it is preferred to set the cation ratio [Ba 2+ /(Si 4+ +B 3+ +Ti 4+ +Nb 5+ +W 6+ )] to the above range.
在第1實施方式中，Ba 2+、Sr 2+及Li +的合計含量與Si 4+、Ti 4+、Nb 5+及W 6+的合計含量的陽離子比[(Ba 2++Sr 2++Li +)/(Si 4++Ti 4++Nb 5++W 6+)]的下限較佳為0.70，進一步以0.75、0.80、0.85、0.90、0.95、0.97、0.98、1.00、1.02，1.04、1.06的順序更佳。另外，該陽離子比的上限較佳為3.00，進一步以2.50、2.00、1.70、1.50、1.30的順序更佳。 In the first embodiment, the lower limit of the cation ratio of the total content of Ba 2+ , Sr 2+ and Li + to the total content of Si 4+ , Ti 4+ , Nb 5+ and W 6+ [(Ba 2+ +Sr 2+ +Li + )/(Si 4+ +Ti 4+ +Nb 5+ +W 6+ )] is preferably 0.70, and more preferably in the order of 0.75, 0.80, 0.85, 0.90, 0.95, 0.97, 0.98, 1.00, 1.02, 1.04, and 1.06. In addition, the upper limit of the cation ratio is preferably 3.00, and more preferably in the order of 2.50, 2.00, 1.70, 1.50, and 1.30.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點考慮， 較佳將陽離子比[(Ba 2++Sr 2++Li +)/(Si 4++Ti 4++Nb 5++W 6+)]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient αL , a high refractive index and low dispersion, the cation ratio [(Ba 2+ +Sr 2+ +Li + )/(Si 4+ +Ti 4+ +Nb 5+ +W 6+ )] is preferably set to the above range.
在第1實施方式中，Li +、Na +、K +、Cs +、Ca 2+、Ba 2+及Sr 2+的合計含量與Si 4+、Ti 4+、Nb 5+及W 6+的合計含量的陽離子比[(Li ++Na ++K ++Cs ++Ca 2++Ba 2++Sr 2+)/(Si 4++Ti 4++Nb 5++W 6+)]的下限較佳為0.70，進一步以0.75、0.80、0.85、0.90、0.95、0.97、0.98、1.00、1.02、1.04、1.06的順序更佳。另外，該陽離子比的上限較佳為3.00，進一步以2.50、2.00、1.70、1.50、1.30的順序更佳。 In the first embodiment, the lower limit of the cation ratio of the total content of Li + , Na + , K + , Cs + , Ca 2+ , Ba 2+ and Sr 2+ to the total content of Si 4+ , Ti 4+ , Nb 5+ and W 6+ [(Li + +Na + +K + +Cs + +Ca 2+ +Ba 2+ +Sr 2+ )/(Si 4+ +Ti 4+ +Nb 5+ +W 6+ )] is preferably 0.70, and is further preferably 0.75, 0.80, 0.85, 0.90, 0.95, 0.97, 0.98, 1.00, 1.02, 1.04, and 1.06 in the order of. In addition, the upper limit of the cation ratio is preferably 3.00, and more preferably in the order of 2.50, 2.00, 1.70, 1.50, and 1.30.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點考慮，較佳將陽離子比[(Li ++Na ++K ++Cs ++Ca 2++Ba 2++Sr 2+)/(Si 4++Ti 4++Nb 5++W 6+)]設為上述範圍。 From the perspective of obtaining an optical glass with a large average linear expansion coefficient αL , high refractive index and low dispersion, it is preferable to set the cation ratio [(Li + +Na + +K + +Cs + +Ca 2+ +Ba 2+ +Sr 2+ )/(Si 4+ +Ti 4+ +Nb 5+ +W 6+ )] to the above range.
在第1實施方式中，Zn 2+、Gd 3+、Ti 4+、Nb 5+及W 6+的合計含量[Zn 2++Gd 3++Ti 4++Nb 5++W 6+]的上限較佳為20%，進一步以15%、12%、10%、9%、8%、7%的順序更佳。另外，該合計含量的下限較佳為0%，進一步以1%、2%、3%、4%、5%、6%的順序更佳。該合計含量可以為0。 In the first embodiment, the upper limit of the total content of Zn 2+ , Gd 3+ , Ti 4+ , Nb 5+ and W 6+ [Zn 2+ +Gd 3+ +Ti 4+ +Nb 5+ +W 6+ ] is preferably 20%, and more preferably in the order of 15%, 12%, 10%, 9%, 8%, and 7%. In addition, the lower limit of the total content is preferably 0%, and more preferably in the order of 1%, 2%, 3%, 4%, 5%, and 6%. The total content may be 0.
從得到平均線膨脹係數α L大、色散小的光學玻璃的觀點考慮，較佳將合計含量[Zn 2++Gd 3++Ti 4++Nb 5++W 6+]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L and small dispersion, it is preferred that the total content [Zn 2+ +Gd 3+ +Ti 4+ +Nb 5+ +W 6+ ] be within the above range.
在第1實施方式中，Si 4+、Zn 2+、Gd 3+、Ti 4+、Nb 5+及W 6+的合計含量[Si 4++Zn 2++Gd 3++Ti 4++Nb 5++W 6+]的上限較佳為30%，進一步以28%、26%、24%、22%、20%的順序更佳。另外，該合計含量的下限較佳為5%，進一步以8%、10%、12%、14%、15%的順序更佳。 In the first embodiment, the upper limit of the total content of Si 4+ , Zn 2+ , Gd 3+ , Ti 4+ , Nb 5+ and W 6+ [Si 4+ +Zn 2+ +Gd 3+ +Ti 4+ +Nb 5+ +W 6+ ] is preferably 30%, and more preferably in the order of 28%, 26%, 24%, 22%, and 20%. In addition, the lower limit of the total content is preferably 5%, and more preferably in the order of 8%, 10%, 12%, 14%, and 15%.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點考慮，較佳將合計含量[Si 4++Zn 2++Gd 3++Ti 4++Nb 5++W 6+]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L , a high refractive index and low dispersion, it is preferred to set the total content [Si 4+ +Zn 2+ +Gd 3+ +Ti 4+ +Nb 5+ +W 6+ ] to be within the above range.
在第1實施方式中，Si 4+、Zn 2+、Gd 3+、Zr 4+、Ti 4+、Nb 5+及W 6+的合計含量[Si 4++Zn 2++Gd 3++Zr 4++Ti 4++Nb 5++W 6+]的上限較佳為30%，進一步以28%、26%、24%、22%、20%的順序更佳。另外，該合計含量的下限較佳為5%，進一步以8%、10%、12%、14%、15%的順序更佳。 In the first embodiment, the upper limit of the total content of Si 4+ , Zn 2+ , Gd 3+ , Zr 4+ , Ti 4+ , Nb 5+ and W 6+ [Si 4+ +Zn 2+ +Gd 3+ +Zr 4+ +Ti 4+ +Nb 5+ +W 6+ ] is preferably 30%, and more preferably in the order of 28%, 26%, 24%, 22%, and 20%. In addition, the lower limit of the total content is preferably 5%, and more preferably in the order of 8%, 10%, 12%, 14%, and 15%.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點考慮，較佳將合計含量[Si 4++Zn 2++Gd 3++Zr 4++Ti 4++Nb 5++W 6+]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L , a high refractive index and low dispersion, it is preferred to set the total content [Si 4+ +Zn 2+ +Gd 3+ +Zr 4+ +Ti 4+ +Nb 5+ +W 6+ ] to be within the above range.
在第1實施方式中，Al 3+、Si 4+、Zn 2+、Gd 3+、Zr 4+、Ti 4+、Nb 5+及W 6+的合計含量[Al 3++Si 4++Zn 2++Gd 3++Zr 4++Ti 4++Nb 5++W 6+]的上限較佳為30%，進一步以28%、26%、24%、22%、20%的順序更佳。另外，該合計含量的下限較佳為5%，進一步以8%、10%、12%、14%、15%的順序更佳。 In the first embodiment, the upper limit of the total content of Al 3+ , Si 4+ , Zn 2+ , Gd 3+ , Zr 4+ , Ti 4+ , Nb 5+ and W 6+ [Al 3+ +Si 4+ +Zn 2+ +Gd 3+ +Zr 4+ +Ti 4+ +Nb 5+ +W 6+ ] is preferably 30%, and more preferably in the order of 28%, 26%, 24%, 22%, and 20%. In addition, the lower limit of the total content is preferably 5%, and more preferably in the order of 8%, 10%, 12%, 14%, and 15%.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點考慮，較佳將合計含量[Al 3++Si 4++Zn 2++Gd 3++Zr 4++Ti 4++Nb 5++W 6+]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L , a high refractive index and low dispersion, it is preferred to set the total content [Al 3+ +Si 4+ +Zn 2+ +Gd 3+ +Zr 4+ +Ti 4+ +Nb 5+ +W 6+ ] to be within the above range.
在第1實施方式中，La 3+、Y 3+及Ba 2+的合計含量[La 3++Y 3++Ba 2+]的下限較佳為30%，進一步以32%、34%、36%、38%、40%的順序更佳。另外，該合計含量的上限較佳為60%，進一步以58%、56%、54%、52%、50%、48%的順序更佳。 In the first embodiment, the lower limit of the total content of La 3+ , Y 3+ and Ba 2+ [La 3+ +Y 3+ +Ba 2+ ] is preferably 30%, and more preferably in the order of 32%, 34%, 36%, 38%, and 40%. In addition, the upper limit of the total content is preferably 60%, and more preferably in the order of 58%, 56%, 54%, 52%, 50%, and 48%.
從抑制平均線膨脹係數α L的降低、並且得到高折射率低色散性的光學玻璃的觀點考慮，較佳將合計含量[La 3++Y 3++Ba 2+]設為上述範圍。 From the viewpoint of suppressing a decrease in the average linear expansion coefficient α L and obtaining an optical glass with a high refractive index and low dispersion, the total content [La 3+ +Y 3+ +Ba 2+ ] is preferably within the above range.
在第1實施方式的光學玻璃中，Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+及Bi 3+的合計含量的下限較佳為0%，進一步以1%、2%、3%、4%、5%、6%的順序更佳。該合計含量也可以為0%。另外，該合計含量的上限較佳為20%，進一步以15%、12%、10%、9%、8%、7%的順序更佳。 In the optical glass of the first embodiment, the lower limit of the total content of Gd 3+ , Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Bi 3+ is preferably 0%, and more preferably in the order of 1%, 2%, 3%, 4%, 5%, and 6%. The total content may also be 0%. In addition, the upper limit of the total content is preferably 20%, and more preferably in the order of 15%, 12%, 10%, 9%, 8%, and 7%.
從平均線膨脹係數α L大、抑制玻璃的熱穩定性的降低的觀點考慮，Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+、Bi 3+的合計含量較佳設為上述範圍。 From the viewpoint of increasing the average linear expansion coefficient α L and suppressing a decrease in the thermal stability of the glass, the total content of Gd 3+ , Zn 2+ , Ti 4+ , Nb 5+ , W 6+ , and Bi 3+ is preferably within the above range.
在第1實施方式中，La 3+、Gd 3+及Y 3+的合計含量的下限較佳為15%，進一步以16%、17%、18%、19%、20%、21%的順序更佳。另外，該合計含量的上限較佳為40%，進一步以38%、36%、34%、32%、30%、28%的順序更佳。 In the first embodiment, the lower limit of the total content of La 3+ , Gd 3+ and Y 3+ is preferably 15%, and more preferably in the order of 16%, 17%, 18%, 19%, 20%, and 21%. In addition, the upper limit of the total content is preferably 40%, and more preferably in the order of 38%, 36%, 34%, 32%, 30%, and 28%.
從得到高折射率低色散的光學玻璃的觀點考慮，La 3+、Gd 3+及Y 3+的合計含量較佳設為上述範圍。 From the viewpoint of obtaining an optical glass with a high refractive index and low dispersion, the total content of La 3+ , Gd 3+ , and Y 3+ is preferably set to be within the above range.
在第1實施方式中，B 3+的含量、Si 4+的含量的2倍、Al 3+的含量的合計[B 3++(2×Si 4+)+Al 3+]的下限較佳為0.20%，進一步以0.25%、0.30%、0.35%、0.37%、0.38%的順序更佳。另外，該合計的上限較佳為0.65%，進一步以0.60%、0.55%、0.53%的順序更佳。 In the first embodiment, the lower limit of the total content of B 3+ , twice the content of Si 4+ , and the content of Al 3+ [B 3+ +(2×Si 4+ )+Al 3+ ] is preferably 0.20%, and more preferably in the order of 0.25%, 0.30%, 0.35%, 0.37%, and 0.38%. In addition, the upper limit of the total is preferably 0.65%, and more preferably in the order of 0.60%, 0.55%, and 0.53%.
Si 4+是特別地降低折射率的成分，因此，從盡可能不降低折射率、而得到高折射率低色散的光學玻璃的觀點考慮，合計[B 3++(2×Si 4+)+Al 3+]較佳設為上述範圍。 Si 4+ is a component that particularly lowers the refractive index. Therefore, from the viewpoint of obtaining a high-refractive-index, low-dispersion optical glass without lowering the refractive index as much as possible, the total [B 3+ +(2×Si 4+ )+Al 3+ ] is preferably set to be within the above range.
在第1實施方式中，La 3+、Gd 3+及Y 3+的合計含量與B 3+、Si 4+及Al 3+的合計含量的陽離子比[(La 3++Gd 3++Y 3+)/(B 3++Si 4++Al 3+)]的下限較佳為0.40，進一步以0.44、0.46、0.47的順序更佳。另外，該陽離子比的上限較佳為0.80，進一步以0.76、0.74、0.70、0.68、0.66的順序更佳。 In the first embodiment, the lower limit of the cation ratio of the total content of La 3+ , Gd 3+ and Y 3+ to the total content of B 3+ , Si 4+ and Al 3+ [(La 3+ +Gd 3+ +Y 3+ )/(B 3+ +Si 4+ +Al 3+ )] is preferably 0.40, and more preferably in the order of 0.44, 0.46, and 0.47. In addition, the upper limit of the cation ratio is preferably 0.80, and more preferably in the order of 0.76, 0.74, 0.70, 0.68, and 0.66.
從得到高折射率低色散的光學玻璃的觀點考慮，陽離子比[(La 3++Gd 3++Y 3+)/(B 3++Si 4++Al 3+)]較佳設為上述範圍。 From the viewpoint of obtaining an optical glass with a high refractive index and low dispersion, the cation ratio [(La 3+ +Gd 3+ +Y 3+ )/(B 3+ +Si 4+ +Al 3+ )] is preferably set to be within the above range.
在第1實施方式中，B 3+、Si 4+及Al 3+的合計含量的下限較佳為30%，進一步以35%、38%、40%、41%、42%的順序更佳。另外，該合計含量的上限較佳為65%，進一步以60%、58%、56%的順序更佳。 In the first embodiment, the lower limit of the total content of B 3+ , Si 4+ and Al 3+ is preferably 30%, more preferably in the order of 35%, 38%, 40%, 41%, and 42%. In addition, the upper limit of the total content is preferably 65%, more preferably in the order of 60%, 58%, and 56%.
從得到平均線膨脹係數α L大、高折射率低色散的光學玻璃的觀點考慮，B 3+、Si 4+及Al 3+的合計含量較佳設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L , a high refractive index and low dispersion, the total content of B 3+ , Si 4+ and Al 3+ is preferably set to be within the above range.
在第1實施方式中，La 3+及Y 3+的合計含量與B 3+及Ba 2+的合計含量的陽離子比[(La 3++Y 3+)/(B 3++Ba 2+)]的下限較佳為0.20，進一步以0.25、0.30、0.35的順序更佳。另外，該陽離子比的上限較佳為0.80，進一步以0.75、0.70、0.65的順序更佳。 In the first embodiment, the lower limit of the cation ratio of the total content of La 3+ and Y 3+ to the total content of B 3+ and Ba 2+ [(La 3+ +Y 3+ )/(B 3+ +Ba 2+ )] is preferably 0.20, and more preferably in the order of 0.25, 0.30, and 0.35. In addition, the upper limit of the cation ratio is preferably 0.80, and more preferably in the order of 0.75, 0.70, and 0.65.
從得到高折射率/低色散、平均線膨脹係數α L大的光學玻璃的觀點考慮，陽離子比[(La 3++Y 3+)/(B 3++Ba 2+)]較佳設為上述範圍。 From the viewpoint of obtaining an optical glass having a high refractive index, low dispersion and a large average linear expansion coefficient α L , the cation ratio [(La 3+ +Y 3+ )/(B 3+ +Ba 2+ )] is preferably set to be within the above range.
在第1實施方式中，Y 3+的含量與La 3+、Gd 3+及Y 3+的合計含量的陽離子比[Y 3+/(La 3++Gd 3++Y 3+)]的下限較佳為0.20，進一步以0.25、0.30、0.35的順序更佳。另外，該陽離子比的上限較佳為0.70，進一步以0.67、0.65、0.60的順序更佳。 In the first embodiment, the lower limit of the cation ratio of the content of Y 3+ to the total content of La 3+ , Gd 3+ and Y 3+ [Y 3+ /(La 3+ +Gd 3+ +Y 3+ )] is preferably 0.20, and more preferably in the order of 0.25, 0.30, and 0.35. In addition, the upper limit of the cation ratio is preferably 0.70, and more preferably in the order of 0.67, 0.65, and 0.60.
從保持玻璃的熱穩定性的觀點考慮，陽離子比[Y 3+/(La 3++Gd 3++Y 3+)]較佳設為上述範圍。 From the viewpoint of maintaining the thermal stability of the glass, the cation ratio [Y 3+ /(La 3+ +Gd 3+ +Y 3+ )] is preferably set to be within the above range.
在第1實施方式中，Y 3+的含量與Ti 4+、La 3+及Y 3+的合計含量的陽離子比[Y 3+/(Ti 4++La 3++Y 3+)]的下限較佳為0.20，進一步以0.22、0.24、0.26、0.28的順序更佳。另外，該陽離子比的上限較佳為0.70，進一步以0.65、0.60、0.55、0.50的順序更佳。 In the first embodiment, the lower limit of the cation ratio of the content of Y 3+ to the total content of Ti 4+ , La 3+ and Y 3+ [Y 3+ /(Ti 4+ +La 3+ +Y 3+ )] is preferably 0.20, and more preferably in the order of 0.22, 0.24, 0.26, and 0.28. In addition, the upper limit of the cation ratio is preferably 0.70, and more preferably in the order of 0.65, 0.60, 0.55, and 0.50.
提高玻璃的高折射低色散性、保持熱穩定性及得到期望的光學常數的觀點考慮，陽離子比[Y 3+/(Ti 4++La 3++Y 3+)]較佳設為上述範圍。 From the viewpoint of improving the high refractive index and low dispersion of the glass, maintaining thermal stability, and obtaining desired optical constants, the cation ratio [Y 3+ /(Ti 4+ +La 3+ +Y 3+ )] is preferably set to the above range.
在第1實施方式的光學玻璃中，Si 4+的含量的下限較佳為0%，進一步以5%、7%、9%、10%的順序更佳。另外，Si 4+的含量的上限較佳為30%，進一步以25%、20%、18%、16%、15%、14%、13%的順序更佳。 In the optical glass of the first embodiment, the lower limit of the content of Si 4+ is preferably 0%, and more preferably in the order of 5%, 7%, 9%, and 10%. In addition, the upper limit of the content of Si 4+ is preferably 30%, and more preferably in the order of 25%, 20%, 18%, 16%, 15%, 14%, and 13%.
Si 4+為玻璃的網絡形成成分，具有改善玻璃的熱穩定性、化學耐久性、耐候性、提高熔融玻璃的黏度、容易將熔融玻璃成型的作用。另一方面，Si 4+的含量多時，除了平均線膨脹係數α L降低以外，還存在折射率nd降低之虞。因此，Si 4+的含量較佳為上述範圍。 Si 4+ is a network-forming component of glass, and has the effects of improving the thermal stability, chemical durability, and weather resistance of glass, increasing the viscosity of molten glass, and facilitating the molding of molten glass. On the other hand, when the content of Si 4+ is high, in addition to reducing the average linear expansion coefficient α L , there is also a risk of reducing the refractive index nd. Therefore, the content of Si 4+ is preferably within the above range.
在第1實施方式的光學玻璃中，B 3+的含量的下限較佳為20%，進一步以25%、28%、29%、30%、31%、32%的順序更佳。另外，B 3+的含量的上限較佳為50%，進一步以45%、43%、41%、40%、39%、38%、37%、36%的順序更佳。 In the optical glass of the first embodiment, the lower limit of the content of B 3+ is preferably 20%, and more preferably in the order of 25%, 28%, 29%, 30%, 31%, and 32%. In addition, the upper limit of the content of B 3+ is preferably 50%, and more preferably in the order of 45%, 43%, 41%, 40%, 39%, 38%, 37%, and 36%.
B 3+為玻璃的網絡形成成分，具有改善玻璃的熱穩定性的作用。另外，是在網絡形成成分中不會降低平均線膨脹係數α L的成分。另一方面，B 3+的含量多時，存在折射率nd降低之虞。因此，B 3+的含量較佳為上述範圍。 B 3+ is a network-forming component of glass and has the effect of improving the thermal stability of glass. In addition, it is a component that does not reduce the average linear expansion coefficient α L among network-forming components. On the other hand, when the content of B 3+ is high, there is a risk of reducing the refractive index nd. Therefore, the content of B 3+ is preferably within the above range.
在第1實施方式的光學玻璃中，Al 3+的含量的上限較佳為5%，進一步以4%、3%、2%、1%的順序更佳。另外，Al 3+的含量的下限較佳為0%。Al 3+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Al 3+ is preferably 5%, and more preferably in the order of 4%, 3%, 2%, and 1%. In addition, the lower limit of the content of Al 3+ is preferably 0%. The content of Al 3+ may also be 0%.
Al 3+是具有改善玻璃的化學耐久性、耐候性的作用的玻璃成分，可以認為是網絡形成成分。另一方面，Al 3+的含量變多時，存在折射率nd降低、玻璃的熱穩定性及熔融性降低之虞。因此，Al 3+的含量較佳為上述範圍。 Al 3+ is a glass component that improves the chemical durability and weather resistance of glass and can be considered as a network-forming component. On the other hand, when the content of Al 3+ increases, there is a risk of lowering the refractive index nd and lowering the thermal stability and solubility of the glass. Therefore, the content of Al 3+ is preferably within the above range.
在第1實施方式的光學玻璃中，P 5+的含量的上限較佳為4%，進一步以3%、2%、1%、0.8%的順序更佳。另外，P 5+的含量的下限較佳為0%。P 5+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of P 5+ is preferably 4%, and more preferably in the order of 3%, 2%, 1%, and 0.8%. In addition, the lower limit of the content of P 5+ is preferably 0%. The content of P 5+ may also be 0%.
P 5+是降低折射率nd的成分，此外，也是降低玻璃的熱穩定性的成分。因此，P 5+的含量較佳為上述範圍。 P 5+ is a component that reduces the refractive index nd and also a component that reduces the thermal stability of glass. Therefore, the content of P 5+ is preferably within the above range.
在第1實施方式的光學玻璃中，Li +的含量的上限較佳為20%，進一步以18%、16%、14%、12%、10%、8%、6%、4%、2%、1%的順序更佳。另外，Li +的含量的下限較佳為0%，進一步以0.1%、0.5%、0.8%的順序更佳。Li +的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Li + is preferably 20%, and more preferably in the order of 18%, 16%, 14%, 12%, 10%, 8%, 6%, 4%, 2%, and 1%. In addition, the lower limit of the content of Li + is preferably 0%, and more preferably in the order of 0.1%, 0.5%, and 0.8%. The content of Li + may also be 0%.
Li +是有助於玻璃的低比重化的成分，具有改善玻璃的熔融性、並且增大平均線膨脹係數α L的作用。此外，是有助於玻璃化轉變溫度Tg的降低的成分，在精密壓製成型時有助於成型性的提高。另一方面，Li +的含量變多時，耐失透性、耐酸性降低。因此，Li +的含量較佳為上述範圍。 Li + is a component that contributes to the lowering of the specific gravity of glass, has the effect of improving the melting property of glass and increasing the average linear expansion coefficient α L. In addition, it is a component that contributes to the reduction of the glass transition temperature Tg, and contributes to the improvement of the formability during precision press molding. On the other hand, when the content of Li + increases, the resistance to devitrification and acid resistance decreases. Therefore, the content of Li + is preferably within the above range.
在第1實施方式的光學玻璃中，Na +的含量的上限較佳為30%，進一步以25%、20%、15%、10%、7%、5%、3%、1%的順序更佳。另外，Na +的含量的下限較佳為0%。的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Na + is preferably 30%, and more preferably in the order of 25%, 20%, 15%, 10%, 7%, 5%, 3%, and 1%. In addition, the lower limit of the content of Na + is preferably 0%. The content of can also be 0%.
在第1實施方式的光學玻璃中，K +的含量的上限較佳為30%，進一步以25%、20%、15%、10%、7%、5%、3%、1%的順序更佳。另外，K +的含量的下限較佳為0%。K +的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of K + is preferably 30%, and more preferably in the order of 25%, 20%, 15%, 10%, 7%, 5%, 3%, and 1%. In addition, the lower limit of the content of K + is preferably 0%. The content of K + may also be 0%.
在第1實施方式的光學玻璃中，Na +及K +的合計含量的上限較佳為30%，進一步以25%、20%、15%、10%、7%、5%、3%、1%的順序更佳。另外，該合計含量的下限較佳為0%。該合計含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the total content of Na + and K + is preferably 30%, and more preferably in the order of 25%, 20%, 15%, 10%, 7%, 5%, 3%, and 1%. In addition, the lower limit of the total content is preferably 0%. The total content may also be 0%.
Na +、K +均具有改善玻璃的熔融性的作用。另外，具有增大平均線膨脹係數的作用。另一方面，它們的含量變多時，熱穩定性、耐失透性、化學耐久性、耐候性降低，玻璃成分的揮發性上升。因此，Na +及K +的各含量及其合計含量較佳為上述範圍。 Both Na + and K + have the effect of improving the melting property of glass. In addition, they have the effect of increasing the average linear expansion coefficient. On the other hand, when their contents increase, thermal stability, devitrification resistance, chemical durability, and weather resistance decrease, and volatility of glass components increases. Therefore, the contents of each of Na + and K + and their total content are preferably within the above range.
在第1實施方式的光學玻璃中，Cs +的含量的上限較佳為30%，進一步以25%、20%、15%、10%、7%、5%、3%、1%的順序更佳。另外，Cs +的含量的下限較佳為0%。Cs +的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Cs + is preferably 30%, and more preferably in the order of 25%, 20%, 15%, 10%, 7%, 5%, 3%, and 1%. In addition, the lower limit of the content of Cs + is preferably 0%. The content of Cs + may also be 0%.
Cs +具有改善玻璃的熔融性的作用，但其含量變多時，玻璃的熱穩定性、折射率nd降低，另外，在熔解中，玻璃成分的揮發增加，存在無法得到期望的玻璃之虞。因此，Cs +的含量較佳為上述範圍。 Cs + has the effect of improving the melting property of glass, but when its content increases, the thermal stability and refractive index nd of the glass decrease. In addition, during melting, the volatility of glass components increases, and there is a risk that the desired glass cannot be obtained. Therefore, the content of Cs + is preferably within the above range.
在第1實施方式的光學玻璃中，Li +、Na +、K +及Cs +的合計含量的上限較佳為30%，進一步以25%、20%、15%、13%、12%、11%、10%的順序更佳。另外，該合計含量的下限較佳為0%。該合計含量也可以為0%。從抑制玻璃的液相溫度上升的觀點考慮，Li +、Na +、K +及Cs +的合計含量較佳設為上述範圍。 In the optical glass of the first embodiment, the upper limit of the total content of Li + , Na + , K + and Cs + is preferably 30%, and more preferably in the order of 25%, 20%, 15%, 13%, 12%, 11%, and 10%. In addition, the lower limit of the total content is preferably 0%. The total content may also be 0%. From the viewpoint of suppressing the increase in the liquidus temperature of the glass, the total content of Li + , Na + , K + and Cs + is preferably set to the above range.
在第1實施方式的光學玻璃中，Mg 2+的含量的上限較佳為10%，進一步以8%、6%、4%、2%的順序更佳。另外，Mg 2+的含量的下限較佳為0%。Mg 2+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Mg 2+ is preferably 10%, and more preferably in the order of 8%, 6%, 4%, and 2%. In addition, the lower limit of the content of Mg 2+ is preferably 0%. The content of Mg 2+ may also be 0%.
在第1實施方式的光學玻璃中，Ca 2+的含量的上限較佳為10%，進一步以8%、6%、4%、2%的順序更佳。另外，Ca 2+的含量的下限較佳為0%。Ca 2+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the Ca 2+ content is preferably 10%, and more preferably in the order of 8%, 6%, 4%, and 2%. In addition, the lower limit of the Ca 2+ content is preferably 0%. The Ca 2+ content may also be 0%.
在第1實施方式的光學玻璃中，Sr 2+的含量的上限較佳為20%，進一步以15%、10%、8%、6%、4%、2%、1%、0.5%、0.3%的順序更佳。另外，Sr 2+的含量的下限較佳為0%。Sr 2+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the Sr 2+ content is preferably 20%, and more preferably in the order of 15%, 10%, 8%, 6%, 4%, 2%, 1%, 0.5%, and 0.3%. In addition, the lower limit of the Sr 2+ content is preferably 0%. The Sr 2+ content may also be 0%.
在第1實施方式的光學玻璃中，Mg 2+、Ca 2+及Sr 2+的合計含量的上限較佳為20%，進一步以15%、10%、8%、6%、4%、2%、1%、0.5%、0.3%的順序更佳。另外，該合計含量的下限較佳為0%。該合計含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the total content of Mg 2+ , Ca 2+ and Sr 2+ is preferably 20%, and more preferably in the order of 15%, 10%, 8%, 6%, 4%, 2%, 1%, 0.5%, and 0.3%. In addition, the lower limit of the total content is preferably 0%. The total content may also be 0%.
Mg 2+、Ca 2+、Sr 2+均為具有改善玻璃的熔融性的作用的玻璃成分，按照Sr 2+、Ca 2+、Mg 2+的順序，增大平均線膨脹係數的作用更大。然而，這些玻璃成分的含量變多時，玻璃的熱穩定性及耐失透性降低。因此，這些玻璃成分的各含量及合計含量較佳為上述範圍。 Mg 2+ , Ca 2+ , and Sr 2+ are all glass components that have the effect of improving the melting property of glass. In the order of Sr 2+ , Ca 2+ , and Mg 2+ , the effect of increasing the average linear expansion coefficient is greater. However, when the content of these glass components increases, the thermal stability and devitrification resistance of the glass decrease. Therefore, the content of each of these glass components and the total content are preferably within the above range.
在第1實施方式的光學玻璃中，Ba 2+的含量的下限較佳為5%，進一步以7%、9%、10%、11%、12%、13%、14%的順序更佳。另外，Ba 2+的含量的上限較佳為40%，進一步以35%、30%、28%、26%、25%、24%、23%的順序更佳。 In the optical glass of the first embodiment, the lower limit of the content of Ba 2+ is preferably 5%, and more preferably in the order of 7%, 9%, 10%, 11%, 12%, 13%, and 14%. In addition, the upper limit of the content of Ba 2+ is preferably 40%, and more preferably in the order of 35%, 30%, 28%, 26%, 25%, 24%, and 23%.
Ba 2+是具有增加平均線膨脹係數α L的作用、且不會損害高折射率/低色散特性的玻璃成分。藉由將Ba 2+的含量設為上述範圍，可得到高折射率/低色散、且改善了平均線膨脹係數α L的光學玻璃。另一方面，Ba 2+的含量過多時，存在玻璃的熱穩定性降低、玻璃發生失透之虞。 Ba 2+ is a glass component that has the effect of increasing the average linear expansion coefficient α L without impairing the high refractive index/low dispersion characteristics. By setting the content of Ba 2+ to the above range, an optical glass with high refractive index/low dispersion and improved average linear expansion coefficient α L can be obtained. On the other hand, when the content of Ba 2+ is too high, there is a risk that the thermal stability of the glass is reduced and the glass may become devitrified.
在第1實施方式的光學玻璃中，Si 4+及B 3+的合計含量的上限較佳為60%，進一步以58%、56%、55%、54%的順序更佳。另外，該合計含量的下限較佳為30%，進一步以32%、34%、36%、38%、40%、42%、44%的順序更佳。 In the optical glass of the first embodiment, the upper limit of the total content of Si 4+ and B 3+ is preferably 60%, and more preferably in the order of 58%, 56%, 55%, and 54%. In addition, the lower limit of the total content is preferably 30%, and more preferably in the order of 32%, 34%, 36%, 38%, 40%, 42%, and 44%.
從保持玻璃的穩定性、並且抑制折射率的降低的觀點考慮，Si 4+及B 3+的合計含量較佳設為上述範圍。 From the viewpoint of maintaining the stability of the glass and suppressing the decrease in the refractive index, the total content of Si 4+ and B 3+ is preferably set to the above range.
在第1實施方式的光學玻璃中，Ba 2+的含量與Si 4+及B 3+的合計含量的陽離子比[Ba 2+/(Si 4++B 3+)]的上限較佳為0.60，進一步以0.55、0.50、0.45的順序更佳。另外，該陽離子比的下限較佳為0.25，進一步以0.27、0.29、0.31、0.33、0.35、0.36的順序更佳。 In the optical glass of the first embodiment, the upper limit of the cation ratio of the content of Ba 2+ to the total content of Si 4+ and B 3+ [Ba 2+ /(Si 4+ +B 3+ )] is preferably 0.60, and more preferably in the order of 0.55, 0.50, and 0.45. In addition, the lower limit of the cation ratio is preferably 0.25, and more preferably in the order of 0.27, 0.29, 0.31, 0.33, 0.35, and 0.36.
從得到可保持玻璃的穩定性、並且平均線膨脹係數α L大的玻璃的觀點考慮，該陽離子比較佳設為上述範圍。 From the perspective of obtaining glass that can maintain glass stability and has a large average linear expansion coefficient αL , the cation content is preferably set to the above range.
在第1實施方式的光學玻璃中，Zn 2+的含量的上限較佳為20%，進一步以15%、10%、5%、3%、2%、1%的順序更佳。另外，Zn 2+的含量的下限較佳為0%。Zn 2+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Zn2 + is preferably 20%, and more preferably in the order of 15%, 10%, 5%, 3%, 2%, and 1%. In addition, the lower limit of the content of Zn2 + is preferably 0%. The content of Zn2+ may also be 0%.
Zn 2+是具有改善玻璃的熔融性的作用的玻璃成分。然而，Zn 2+的含量過多時，存在玻璃的比重增大、平均線膨脹係數α L降低之虞。另外，還存在損害玻璃的低色散性之虞。此外，還存在玻璃化轉變溫度Tg降低之虞。因此，Zn 2+的含量較佳為上述範圍。 Zn 2+ is a glass component that improves the melting property of glass. However, when the content of Zn 2+ is too high, there is a risk that the specific gravity of the glass increases and the average linear expansion coefficient α L decreases. In addition, there is a risk that the low dispersion of the glass is impaired. In addition, there is a risk that the glass transition temperature Tg decreases. Therefore, the content of Zn 2+ is preferably within the above range.
在第1實施方式的光學玻璃中，La 3+的含量的下限較佳為5%，進一步以6%、7%、8%、9%、10%、11%的順序更佳。另外，La 3+的含量的上限較佳為30%，進一步以25%、22%、20%、18%、17%的順序更佳。 In the optical glass of the first embodiment, the lower limit of the content of La 3+ is preferably 5%, and more preferably in the order of 6%, 7%, 8%, 9%, 10%, and 11%. In addition, the upper limit of the content of La 3+ is preferably 30%, and more preferably in the order of 25%, 22%, 20%, 18%, and 17%.
La 3+是具有抑制阿貝數νd的減少並提高折射率的作用的玻璃成分。因此，藉由將La 3+的含量設為上述範圍，可得到高折射率/低色散、抑制了平均線膨脹係數α L的降低、並且抑制了相對折射率的溫度係數(dn/dT)的增大的光學玻璃。 La 3+ is a glass component that has the effect of suppressing the decrease of the Abbe number νd and increasing the refractive index. Therefore, by setting the content of La 3+ to the above range, an optical glass with high refractive index/low dispersion, suppressed decrease in the average linear expansion coefficient α L , and suppressed increase in the temperature coefficient of relative refractive index (dn/dT) can be obtained.
在第1實施方式的光學玻璃中，Gd 3+的含量的上限較佳為30%，進一步以25%、20%、15%、10%、5%、3%、2%、1%的順序更佳。另外，Gd 3+的含量的下限較佳為0%。Gd 3+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Gd 3+ is preferably 30%, and more preferably in the order of 25%, 20%, 15%, 10%, 5%, 3%, 2%, and 1%. In addition, the lower limit of the content of Gd 3+ is preferably 0%. The content of Gd 3+ may also be 0%.
Gd 3+為高折射/低色散、且能夠抑制平均線膨脹係數α L的降低的成分，但Gd 3+的含量變得過多時，玻璃的比重增大，因而不佳。另外，從原料成本削減的觀點考慮也不利。因此，Gd 3+的含量較佳為上述範圍。 Gd 3+ is a component with high refractive index and low dispersion and can suppress the decrease of the average linear expansion coefficient α L , but when the content of Gd 3+ becomes too high, the specific gravity of the glass increases, which is not good. In addition, it is not good from the perspective of reducing the cost of raw materials. Therefore, the content of Gd 3+ is preferably within the above range.
在第1實施方式的光學玻璃中，Y 3+的含量的下限較佳為0%，進一步以2%、4%、6%、7%、8%、9%、10%的順序更佳。另外，Y 3+的含量的上限較佳為30%，進一步以25%、20%、18%、17%、16%的順序更佳。 In the optical glass of the first embodiment, the lower limit of the content of Y 3+ is preferably 0%, and more preferably in the order of 2%, 4%, 6%, 7%, 8%, 9%, and 10%. In addition, the upper limit of the content of Y 3+ is preferably 30%, and more preferably in the order of 25%, 20%, 18%, 17%, and 16%.
Y 3+是具有抑制阿貝數νd的減少、且提高折射率的作用的成分。另外，在導入了比較多的鹼金屬成分、鹼土金屬成分中的Ba 2+或Sr 2+的本實施方式的玻璃中，Y 3+對於抑制平均線膨脹係數α L的降低、賦予高折射低色散特性而言是有效的成分。另外，還具有改善玻璃的化學耐久性、耐候性、提高玻璃化轉變溫度的作用。另一方面，Y 3+的含量變得過多時，存在玻璃的熱穩定性及耐失透性降低之虞。因此，Y 3+的含量較佳為上述範圍。 Y 3+ is a component that has the effect of suppressing the reduction of the Abbe number νd and increasing the refractive index. In addition, in the glass of the present embodiment into which a relatively large amount of Ba 2+ or Sr 2+ among the alkali metal components and alkaline earth metal components is introduced, Y 3+ is an effective component for suppressing the reduction of the average linear expansion coefficient α L and imparting high refractive and low dispersion characteristics. In addition, it also has the effect of improving the chemical durability and weather resistance of the glass and increasing the glass transition temperature. On the other hand, when the content of Y 3+ becomes too much, there is a risk that the thermal stability and devitrification resistance of the glass will be reduced. Therefore, the content of Y 3+ is preferably within the above range.
在第1實施方式的光學玻璃中，Zr 4+的含量的上限較佳為10%，進一步以9%、8%、7%、6%、5%、4%、3%、2.5%、2%、1.8%的順序更佳。另外，Zr 4+的含量的下限較佳為0%，進一步以0.005%、0.01%、0.05%、0.1%、0.5%、1.0%、1.5%的順序更佳。Zr 4+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Zr 4+ is preferably 10%, and more preferably in the order of 9%, 8%, 7%, 6%, 5%, 4%, 3%, 2.5%, 2%, and 1.8%. In addition, the lower limit of the content of Zr 4+ is preferably 0%, and more preferably in the order of 0.005%, 0.01%, 0.05%, 0.1%, 0.5%, 1.0%, and 1.5%. The content of Zr 4+ may also be 0%.
Zr 4+是具有提高折射率的作用的成分，藉由適量含有Zr 4+，還具有改善玻璃的熱穩定性的作用。然而，Zr 4+除了是使平均線膨脹係數α L比較小的成分以外，也是增大相對折射率的溫度係數(dn/dT)的溫度依賴性的成分。另外，Zr 4+含量過多時，存在熱穩定性顯著降低之虞。因此，Zr 4+的含量較佳為上述範圍。 Zr 4+ is a component that has the effect of increasing the refractive index. By containing an appropriate amount of Zr 4+ , it also has the effect of improving the thermal stability of the glass. However, Zr 4+ is not only a component that makes the average linear expansion coefficient α L relatively small, but also a component that increases the temperature dependence of the temperature coefficient of relative refractive index (dn/dT). In addition, when the Zr 4+ content is too high, there is a risk that the thermal stability will be significantly reduced. Therefore, the Zr 4+ content is preferably within the above range.
在第1實施方式的光學玻璃中，Ti 4+的含量的上限較佳為15%，進一步以12%、10%、8%、7%的順序更佳。另外，Ti 4+的含量的下限較佳為0%，進一步以1%、2%、3%、4%、5%、6%的順序更佳。Ti 4+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Ti 4+ is preferably 15%, and more preferably in the order of 12%, 10%, 8%, and 7%. In addition, the lower limit of the content of Ti 4+ is preferably 0%, and more preferably in the order of 1%, 2%, 3%, 4%, 5%, and 6%. The content of Ti 4+ may also be 0%.
Ti 4+是具有提高折射率的作用的成分，藉由適量含有Ti 4+，還具有改善玻璃的熱穩定性的作用。另一方面，Ti 4+的含量過多時，除了存在平均線膨脹係數α L降低之虞以外，還存在阿貝數νd降低之虞，另外還存在玻璃的著色變強、進而熔融性變差之虞。因此，Ti 4+的含量較佳為上述範圍。 Ti 4+ is a component that has the effect of increasing the refractive index. By containing a proper amount of Ti 4+ , it also has the effect of improving the thermal stability of the glass. On the other hand, when the content of Ti 4+ is too high, in addition to the possibility of reducing the average linear expansion coefficient α L , there is also the possibility of reducing the Abbe number νd, and there is also the possibility of increasing the coloring of the glass and further deteriorating the meltability. Therefore, the content of Ti 4+ is preferably within the above range.
在第1實施方式的光學玻璃中，Nb 5+的含量的上限較佳為30%，進一步以25%、20%、15%、10%、8%、6%、4%、2%、1%、0.5%、0.1%、0.07%、0.05%、0.03%、0.01%的順序更佳。另外，Nb 5+的含量的下限較佳為0%，進一步以0.001%、0.005%、0.008%的順序更佳。Nb 5+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Nb 5+ is preferably 30%, and more preferably in the order of 25%, 20%, 15%, 10%, 8%, 6%, 4%, 2%, 1%, 0.5%, 0.1%, 0.07%, 0.05%, 0.03%, and 0.01%. In addition, the lower limit of the content of Nb 5+ is preferably 0%, and more preferably in the order of 0.001%, 0.005%, and 0.008%. The content of Nb 5+ may also be 0%.
Nb 5+是具有提高折射率的作用的成分，藉由適量含有Nb 5+，還具有改善玻璃的熱穩定性的作用。另一方面，Nb 5+的含量過多時，除了存在平均線膨脹係數α L降低之虞以外，還存在玻璃的著色變強之虞。因此，Nb 5+的含量較佳為上述範圍。 Nb 5+ is a component that has the effect of increasing the refractive index. When Nb 5+ is contained in an appropriate amount, it also has the effect of improving the thermal stability of the glass. On the other hand, when the content of Nb 5+ is too high, in addition to the possibility of reducing the average linear expansion coefficient αL , there is also the possibility of increasing the coloring of the glass. Therefore, the content of Nb 5+ is preferably within the above range.
在第1實施方式的光學玻璃中，W 6+的含量的上限較佳為10%，進一步以5%、3%、2%、1%、0.5%、0.1%的順序更佳。另外，W 6+的含量的下限較佳為0%。W 6+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of W 6+ is preferably 10%, and more preferably in the order of 5%, 3%, 2%, 1%, 0.5%, and 0.1%. In addition, the lower limit of the content of W 6+ is preferably 0%. The content of W 6+ may also be 0%.
W 6+對其它高色散成分具有降低玻璃化轉變溫度Tg的作用，因此，將玻璃軟化成型時、尤其是實施精密壓製時，可以出於降低成型溫度以保護成型模具、其保護膜、成型機的目的而導入W 6+。另一方面，從提高玻璃的透射率的觀點及抑制玻璃的相對折射率的溫度係數(dn/dT)的上升的觀點考慮，W 6+的含量較佳為上述範圍。 W 6+ has the effect of lowering the glass transition temperature Tg of other high-dispersion components. Therefore, when the glass is softened and molded, especially when precision pressing is performed, W 6+ can be introduced for the purpose of lowering the molding temperature to protect the molding mold, its protective film, and the molding machine. On the other hand, from the perspective of improving the transmittance of the glass and suppressing the increase in the temperature coefficient of the relative refractive index (dn/dT) of the glass, the content of W 6+ is preferably within the above range.
在第1實施方式的光學玻璃中，Bi 3+的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%的順序更佳。另外，Bi 3+的含量的下限較佳為0%。Bi 3+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the Bi 3+ content is preferably 10%, and more preferably in the order of 8%, 6%, 4%, 2%, and 1%. In addition, the lower limit of the Bi 3+ content is preferably 0%. The Bi 3+ content may also be 0%.
Bi 3+是提高折射率nd、但降低阿貝數νd的成分。另外，也是容易增大玻璃的著色的成分。因此，Bi 3+的含量較佳為上述範圍。 Bi 3+ is a component that increases the refractive index nd but decreases the Abbe number νd. In addition, it is also a component that tends to increase the coloring of the glass. Therefore, the content of Bi 3+ is preferably within the above range.
在第1實施方式的光學玻璃中，Ta 5+的含量的上限較佳為30%，進一步以25%、20%、15%、10%、7%、5%、3%、1%的順序更佳。另外，Ta 5+的含量的下限較佳為0%。Ta 5+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Ta 5+ is preferably 30%, and more preferably in the order of 25%, 20%, 15%, 10%, 7%, 5%, 3%, and 1%. In addition, the lower limit of the content of Ta 5+ is preferably 0%. The content of Ta 5+ may also be 0%.
Ta 5+是具有改善玻璃的熱穩定性及耐失透性的作用的玻璃成分。另一方面，Ta 5+使折射率上升，使玻璃高色散化。另外，Ta 5+的含量變多時，玻璃的熱穩定性降低，將玻璃熔融時，變得容易發生玻璃原料的熔融殘留。另外，Ta 5+是相對降低平均線膨脹係數α L的成分。因此，Ta 5+的含量較佳為上述範圍。此外，Ta 5+是與其它玻璃成分相比非常昂貴的成分，Ta 5+的含量變多時，玻璃的生產成本增大。此外，Ta 5+的分子量比其它玻璃成分大，因此，會增大玻璃的比重，結果會增大光學元件的重量。 Ta 5+ is a glass component that improves the thermal stability and resistance to devitrification of glass. On the other hand, Ta 5+ increases the refractive index and makes the glass highly dispersed. In addition, when the content of Ta 5+ increases, the thermal stability of the glass decreases, and when the glass is melted, it becomes easy to produce melt residues of the glass raw materials. In addition, Ta 5+ is a component that relatively reduces the average linear expansion coefficient α L. Therefore, the content of Ta 5+ is preferably within the above range. In addition, Ta 5+ is a very expensive component compared to other glass components. When the content of Ta 5+ increases, the production cost of the glass increases. In addition, the molecular weight of Ta 5+ is larger than that of other glass components, so it will increase the specific gravity of the glass, resulting in an increase in the weight of the optical element.
在第1實施方式的光學玻璃中，Sc 3+的含量的上限較佳為3.0%，進一步以2.0%、1.0%的順序更佳。另外，Sc 3+的含量的下限較佳為0%。Sc 3+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Sc 3+ is preferably 3.0%, and more preferably 2.0% and 1.0%. In addition, the lower limit of the content of Sc 3+ is preferably 0%. The content of Sc 3+ may also be 0%.
在第1實施方式的光學玻璃中，Hf 4+的含量的上限較佳為3.0%，進一步以2.0%、1.0%的順序更佳。另外，Hf 4+的含量的下限較佳為0%。Hf 4+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Hf 4+ is preferably 3.0%, and more preferably in the order of 2.0% and 1.0%. In addition, the lower limit of the content of Hf 4+ is preferably 0%. The content of Hf 4+ may also be 0%.
Sc 3+、Hf 4+均具有提高折射率nd的作用，而且是昂貴的成分。因此，Sc 3+、Hf 4+的各含量較佳為上述範圍。 Sc 3+ and Hf 4+ both have the function of increasing the refractive index nd and are expensive components. Therefore, the contents of Sc 3+ and Hf 4+ are preferably within the above ranges.
在第1實施方式的光學玻璃中，Lu 3+的含量的上限較佳為3.0%，進一步以2.0%、1.0%的順序更佳。另外，Lu 3+的含量的下限較佳為0%。需要說明的是，Lu 3+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Lu 3+ is preferably 3.0%, and more preferably 2.0% and 1.0%. In addition, the lower limit of the content of Lu 3+ is preferably 0%. It should be noted that the content of Lu 3+ may also be 0%.
Lu 3+具有提高折射率nd的作用。另外，由於其分子量大，所以也是增加玻璃的比重的玻璃成分。因此，Lu 3+的含量較佳為上述範圍。 Lu 3+ has the effect of increasing the refractive index nd. In addition, due to its large molecular weight, it is also a glass component that increases the specific gravity of the glass. Therefore, the content of Lu 3+ is preferably within the above range.
在第1實施方式的光學玻璃中，Ge 4+的含量的上限較佳為3.0%，進一步以2.0%、1.0%的順序更佳。另外，Ge 4+的含量的下限較佳為0%。Ge 4+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Ge 4+ is preferably 3.0%, and more preferably in the order of 2.0% and 1.0%. In addition, the lower limit of the content of Ge 4+ is preferably 0%. The content of Ge 4+ may also be 0%.
Ge 4+具有提高折射率nd的作用，另外，在通常使用的玻璃成分中，其明顯昂貴的成分。因此，從降低玻璃的製造成本的觀點考慮，Ge 4+的含量較佳為上述範圍。 Ge 4+ has the effect of increasing the refractive index nd, and is a significantly expensive component among commonly used glass components. Therefore, from the perspective of reducing the manufacturing cost of glass, the content of Ge 4+ is preferably within the above range.
在第1實施方式的光學玻璃中，Yb 3+的含量的上限較佳為3.0%，進一步以2.0%、1.0%的順序更佳。另外，Yb 3+的含量的下限較佳為0%。Yb 3+的含量也可以為0%。 In the optical glass of the first embodiment, the upper limit of the content of Yb 3+ is preferably 3.0%, and more preferably in the order of 2.0% and 1.0%. In addition, the lower limit of the content of Yb 3+ is preferably 0%. The content of Yb 3+ may also be 0%.
Yb 3+的含量過多時，存在玻璃的熱穩定性及耐失透性降低之虞。另外，在通常使用的玻璃成分中，其是昂貴的成分。從防止玻璃的熱穩定性的降低、抑制比重的增大的觀點考慮，另外從抑制玻璃的製造成本的觀點考慮，Yb 3+的含量較佳為上述範圍。 When the content of Yb 3+ is too high, the thermal stability and devitrification resistance of the glass may be reduced. In addition, it is an expensive component among the commonly used glass components. From the perspective of preventing the reduction of the thermal stability of the glass and suppressing the increase of the specific gravity, and from the perspective of suppressing the production cost of the glass, the content of Yb 3+ is preferably within the above range.
第1實施方式的光學玻璃的陽離子成分較佳主要由上述的成分、即Si 4+、B 3+、Al 3+、P 5+、Li +、Na +、K +、Cs +、Mg 2+、Ca 2+、Sr 2+、Ba 2+、Zn 2+、La 3+、Gd 3+、Y 3+、Zr 4+、Ti 4+、Nb 5+、W 6+、Bi 3+、Ta 5+、Sc 3+、Hf 4+、Lu 3+、Ge 4+及Yb 3+構成，上述的成分的合計含量較佳為95.0%以上，進一步以98.0%以上、99.0%以上、99.5%以上的順序更佳。 The cationic component of the optical glass of the first embodiment is preferably mainly composed of the above-mentioned components, namely Si 4+ , B 3+ , Al 3+ , P 5+ , Li + , Na + , K + , Cs + , Mg 2+ , Ca 2+ , Sr 2+ , Ba 2+ , Zn 2+ , La 3+ , Gd 3+ , Y 3+ , Zr 4+ , Ti 4+ , Nb 5+ , W 6+ , Bi 3+ , Ta 5+ , Sc 3+ , Hf 4+ , Lu 3+ , Ge 4+ and Yb 3+ , and the total content of the above-mentioned components is preferably 95.0% or more, and more preferably 98.0% or more, 99.0% or more and 99.5% or more in this order.
本實施方式的光學玻璃中，Te 4+的含量的上限較佳為2%，更佳較佳為1%。另外，Te 4+的含量的下限較佳為0%。 In the optical glass of the present embodiment, the upper limit of the content of Te 4+ is preferably 2%, more preferably 1%. In addition, the lower limit of the content of Te 4+ is preferably 0%.
Te 4+的氧化物具有毒性，因而較佳減少Te 4+的含量。因此，Te 4+的含量較佳為上述範圍。 Te 4+ oxide is toxic, so it is better to reduce the content of Te 4+ . Therefore, the content of Te 4+ is preferably within the above range.
第1實施方式的光學玻璃可以包含O 2-作為陰離子成分。O 2-的含量的下限較佳為90陰離子%，進一步以95陰離子%、97陰離子%、98陰離子%的順序更佳。另外，O 2-的含量的上限較佳為100陰離子%，進一步以99.5陰離子%、99陰離子%的順序更佳。O 2-的含量也可以為100陰離子%。 The optical glass of the first embodiment may contain O 2- as an anion component. The lower limit of the content of O 2- is preferably 90 anion%, and more preferably in the order of 95 anion%, 97 anion%, and 98 anion%. In addition, the upper limit of the content of O 2- is preferably 100 anion%, and more preferably in the order of 99.5 anion%, and 99 anion%. The content of O 2- may also be 100 anion%.
在第1實施方式的光學玻璃中，F -的含量的下限較佳為0陰離子%，進一步以0.1陰離子%、0.2陰離子%、0.3陰離子%的順序更佳。F -的含量也可以為0陰離子%。另外，F -的含量的上限較佳為5.0陰離子%，進一步以3.0陰離子%、1.0陰離子%、0.5陰離子%的順序更佳。 In the optical glass of the first embodiment, the lower limit of the content of F- is preferably 0 anion%, and more preferably in the order of 0.1 anion%, 0.2 anion%, and 0.3 anion%. The content of F- may also be 0 anion%. In addition, the upper limit of the content of F- is preferably 5.0 anion%, and more preferably in the order of 3.0 anion%, 1.0 anion%, and 0.5 anion%.
第1實施方式的光學玻璃可以包含F -及O 2-以外的成分作為陰離子成分。作為F -及O 2-以外的陰離子成分，可示例出Cl -、Br -、I -，但Cl -、Br -、I -均容易在玻璃的熔融中揮發。由於這些成分的揮發，會發生玻璃的特性變動、玻璃的均勻性降低、熔融設備的消耗變得顯著等問題。因此，Cl -的含量較佳小於5.0陰離子%，進一步以小於3.0陰離子%、小於1.0陰離子%、小於0.5陰離子%、小於0.3陰離子%的順序更佳。另外，Br -及I -的合計含量較佳小於5.0陰離子%，進一步以小於3.0陰離子%、小於1.0陰離子%、小於0.5陰離子%、小於0.1陰離子%、0陰離子%的順序更佳。 The optical glass of the first embodiment may contain components other than F- and O2- as anion components. Examples of anion components other than F- and O2- include Cl- , Br- , and I- , but Cl- , Br-, and I- are all easily volatile during melting of the glass. Due to the volatility of these components, problems such as changes in glass properties, reduced glass uniformity, and significant consumption of melting equipment may occur. Therefore, the Cl- content is preferably less than 5.0 anion%, and more preferably less than 3.0 anion%, less than 1.0 anion%, less than 0.5 anion%, and less than 0.3 anion%. In addition, the total content of Br- and I- is preferably less than 5.0 anion%, and more preferably less than 3.0 anion%, less than 1.0 anion%, less than 0.5 anion%, less than 0.1 anion%, and 0 anion%.
第1實施方式的光學玻璃較佳基本上由上述成分構成，但也可以在不妨礙本發明的作用效果的範圍中含有其它成分。另外，在本發明中，不排除含有不可避免的雜質。The optical glass of the first embodiment is preferably basically composed of the above components, but may also contain other components within the range that does not hinder the effects of the present invention. In addition, in the present invention, it is not excluded to contain inevitable impurities.
＜其它成分組成＞ Pb、As、Cd、Tl、Be、Se均具有毒性。因此，本實施方式的光學玻璃較佳不含有這些元素作為玻璃成分。 <Other components> Pb, As, Cd, Tl, Be, and Se are all toxic. Therefore, the optical glass of this embodiment preferably does not contain these elements as glass components.
U、Th、Ra均為放射性元素。因此，本實施方式的光學玻璃較佳不含有這些元素作為玻璃成分。U, Th, and Ra are all radioactive elements. Therefore, the optical glass of this embodiment preferably does not contain these elements as glass components.
V、Cr、Mn、Fe、Co、Ni、Cu、Pr、Nd、Pm、Sm、Eu、Tb、Dy、Ho、Er、Tm會增大玻璃的著色，成為荧光的产生源。因此，本實施方式的光學玻璃較佳不含有這些元素作為玻璃成分。V, Cr, Mn, Fe, Co, Ni, Cu, Pr, Nd, Pm, Sm, Eu, Tb, Dy, Ho, Er, and Tm increase the coloring of the glass and become a source of fluorescence. Therefore, the optical glass of the present embodiment preferably does not contain these elements as glass components.
Sb(Sb 2O 3)、Ce(CeO 2)是作為澄清劑發揮功能的可任意添加的元素。其中，Sb(Sb 2O 3)是澄清效果大的澄清劑。關於澄清劑的含量，以下示出換算成氧化物的值。 Sb (Sb 2 O 3 ) and Ce (CeO 2 ) are elements that can be added arbitrarily to function as fining agents. Among them, Sb (Sb 2 O 3 ) is a fining agent with a large fining effect. The content of the fining agent is shown below in terms of the value converted into oxides.
Sb 2O 3的含量以外加比例表示。即，將Sb 2O 3及CeO 2以外的全部玻璃成分的合計含量設為100質量%時的Sb 2O 3的含量較佳小於1質量%、更佳小於0.1質量%。進一步以小於0.05質量%、小於0.03質量%、小於0.02質量%、小於0.01%的順序為佳。Sb 2O 3的含量也可以為0質量%。 The content of Sb2O3 is expressed as an additional ratio. That is, when the total content of all glass components other than Sb2O3 and CeO2 is set to 100 mass%, the content of Sb2O3 is preferably less than 1 mass %, more preferably less than 0.1 mass %. It is further preferably less than 0.05 mass%, less than 0.03 mass%, less than 0.02 mass%, and less than 0.01% in this order. The content of Sb2O3 may also be 0 mass%.
CeO 2的含量也以外加比例表示。即，將CeO 2、Sb 2O 3以外的全部玻璃成分的合計含量設為100質量%時的CeO 2的含量較佳小於2質量%、更佳小於1質量%、進一步較佳小於0.5質量%、更進一步較佳小於0.1質量%的範圍。CeO 2的含量也可以為0質量%。藉由將CeO 2的含量設為上述範圍，能夠改善玻璃的澄清性。 The content of CeO 2 is also expressed as an additional ratio. That is, when the total content of all glass components other than CeO 2 and Sb 2 O 3 is set to 100 mass %, the content of CeO 2 is preferably less than 2 mass %, more preferably less than 1 mass %, further preferably less than 0.5 mass %, and further preferably less than 0.1 mass %. The content of CeO 2 may also be 0 mass %. By setting the content of CeO 2 to the above range, the clarity of the glass can be improved.
(玻璃特性) 接下來，對第1實施方式的光學玻璃的特性進行說明。 (Glass properties) Next, the properties of the optical glass of the first embodiment will be described.
＜折射率nd＞ 在第1實施方式的光學玻璃中，折射率nd較佳為1.70~1.88，更佳較佳為1.73~1.85。折射率nd的下限可以為1.74、1.75、1.76、1.77、1.78或1.79，折射率nd的上限可以為1.84、1.83或1.82。 <Refractive index nd> In the optical glass of the first embodiment, the refractive index nd is preferably 1.70 to 1.88, and more preferably 1.73 to 1.85. The lower limit of the refractive index nd may be 1.74, 1.75, 1.76, 1.77, 1.78 or 1.79, and the upper limit of the refractive index nd may be 1.84, 1.83 or 1.82.
可以藉由適當調整各玻璃成分的含量而將折射率nd設為期望的值。具有相對地提高折射率nd的作用的成分(高折射率化成分)為Nb 5+、Ti 4+、W 6+、Bi 3+、Ta 5+、Zr 4+、La 3+等(即，以氧化物表示為Nb 2O 5、TiO 2、WO 3、Bi 2O 3、Ta 2O 5、ZrO 2、La 2O 3等)。另一方面，具有相對地降低折射率nd的作用的成分(低折射率化成分)為P 5+、Si 4+、B 3+、Li +、Na +、K +等(即，以氧化物表示為P 2O 5、SiO 2、B 2O 3、Li 2O、Na 2O、K 2O等)。 The refractive index nd can be set to a desired value by appropriately adjusting the content of each glass component. Components that have the effect of relatively increasing the refractive index nd (refractive index-increasing components) include Nb 5+ , Ti 4+ , W 6+ , Bi 3+ , Ta 5+ , Zr 4+ , La 3+ , etc. (i.e., Nb 2 O 5 , TiO 2 , WO 3 , Bi 2 O 3 , Ta 2 O 5 , ZrO 2 , La 2 O 3 , etc. in the form of oxides). On the other hand, components that have the effect of relatively decreasing the refractive index nd (refractive index-lowering components) include P 5+ , Si 4+ , B 3+ , Li + , Na + , K + , etc. (i.e., P 2 O 5 , SiO 2 , B 2 O 3 , Li 2 O, Na 2 O, K 2 O, etc. in the form of oxides).
＜阿貝數νd＞ 在第1實施方式的光學玻璃中，阿貝數νd較佳為35~55。阿貝數νd的下限可以為36、37、38、39或40，阿貝數νd的上限可以為53、51、49、47、45、43或42。 <Abbe number νd> In the optical glass of the first embodiment, the Abbe number νd is preferably 35 to 55. The lower limit of the Abbe number νd may be 36, 37, 38, 39 or 40, and the upper limit of the Abbe number νd may be 53, 51, 49, 47, 45, 43 or 42.
可以藉由適當調整各玻璃成分的含量而將阿貝數νd設為期望的值。相對地降低阿貝數νd的成分、即高色散化成分為Nb 5+、Ti 4+、W 6+、Bi 3+、Ta 5+、Zr 4+等(即，以氧化物表示為Nb 2O 5、TiO 2、WO 3、Bi 2O 3、Ta 2O 5、ZrO 2等)。另一方面，相對地提高阿貝數νd的成分、即低色散化成分為P 5+、Si 4+、B 3+、Li +、Na +、K +、La 3+、Ba 2+、Ca 2+、Sr 2+等(即，以氧化物表示為P 2O 5、SiO 2、B 2O 3、Li 2O、Na 2O、K 2O、La 2O 3、BaO、CaO、SrO等)。 The Abbe number νd can be set to a desired value by appropriately adjusting the content of each glass component. Components that relatively reduce the Abbe number νd, i.e., high dispersion components, include Nb 5+ , Ti 4+ , W 6+ , Bi 3+ , Ta 5+ , Zr 4+ , etc. (i.e., Nb 2 O 5 , TiO 2 , WO 3 , Bi 2 O 3 , Ta 2 O 5 , ZrO 2 , etc., expressed as oxides). On the other hand, components that relatively increase the Abbe number νd, i.e., low dispersion components, include P 5+ , Si 4+ , B 3+ , Li + , Na + , K + , La 3+ , Ba 2+ , Ca 2+ , Sr 2+ and the like (i.e., expressed as oxides, P 2 O 5 , SiO 2 , B 2 O 3 , Li 2 O, Na 2 O, K 2 O, La 2 O 3 , BaO, CaO, SrO and the like).
在第1實施方式的光學玻璃中，折射率nd與阿貝數νd較佳滿足下述式(1)，更佳滿足下述式(2)，進一步較佳滿足下述式(3)，特別佳滿足下述式(4)。藉由使折射率nd與阿貝數νd滿足下述式子，可得到具有高折射率/低色散特性的光學玻璃。 nd－(-0.0183×阿貝數νd+2.502)≥0…(1) nd－(-0.0183×阿貝數νd+2.512)≥0…(2) nd－(-0.0183×阿貝數νd+2.522)≥0…(3) nd－(-0.0183×阿貝數νd+2.532)≥0…(4) In the optical glass of the first embodiment, the refractive index nd and the Abbe number νd preferably satisfy the following formula (1), more preferably satisfy the following formula (2), further preferably satisfy the following formula (3), and particularly preferably satisfy the following formula (4). By making the refractive index nd and the Abbe number νd satisfy the following formula, an optical glass having high refractive index/low dispersion characteristics can be obtained. nd－(-0.0183×Abbe number νd+2.502)≥0…(1) nd－(-0.0183×Abbe number νd+2.512)≥0…(2) nd－(-0.0183×Abbe number νd+2.522)≥0…(3) nd－(-0.0183×Abbe number νd+2.532)≥0…(4)
＜平均線膨脹係數α L＞ 在第1實施方式的光學玻璃中，其在-30~70℃下的平均線膨脹係數α L的下限較佳為0.80×10 -5℃ -1，進一步以0.81×10 -5℃ -1、0.82×10 -5℃ -1、0.83×10 -5℃ -1、0.84×10 -5℃ -1、0.85×10 -5℃ -1、0.86×10 -5℃ -1、0.87×10 -5℃ -1、0.88×10 -5℃ -1的順序更佳。另外，從保持玻璃的穩定性、得到期望的光學特性的觀點考慮，平均線膨脹係數α L的上限可示例出1.20×10 -5℃ -1，較佳為1.10×10 -5℃ -1以下，進一步以1.00×10 -5℃ -1、0.98×10 -5℃ -1、0.96×10 -5℃ -1、0.95×10 -5℃ -1、0.94×10 -5℃ -1、0.93×10 -5℃ -1的順序更佳。 <Average Linear Expansion Coefficient α L > In the optical glass of the first embodiment, the lower limit of the average linear expansion coefficient α L at -30 to 70°C is preferably 0.80×10 -5 ℃ -1 , and more preferably in the order of 0.81×10 -5 ℃ -1 , 0.82×10 -5 ℃ -1 , 0.83×10 -5 ℃ -1 , 0.84×10 -5 ℃ -1 , 0.85×10 -5 ℃ -1 , 0.86×10 -5 ℃ -1 , 0.87×10 -5 ℃ -1 , and 0.88×10 -5 ℃ -1 . From the viewpoint of maintaining the stability of the glass and obtaining desired optical properties, the upper limit of the mean linear expansion coefficient α L is 1.20×10 -5 ℃ -1 , preferably 1.10×10 -5 ℃ -1 or less, and more preferably in the order of 1.00×10 -5 ℃ -1 , 0.98×10 -5 ℃ -1 , 0.96×10 -5 ℃ -1 , 0.95×10 -5 ℃ -1 , 0.94×10 -5 ℃ -1 , and 0.93×10 -5 ℃ -1 .
藉由將在-30~70℃下的平均線膨脹係數α L設為上述範圍，可以得到可用於廣泛的溫度環境的光學玻璃。 By setting the average linear expansion coefficient α L at -30 to 70°C to the above range, an optical glass that can be used in a wide range of temperature environments can be obtained.
平均線膨脹係數α L基於日本光學玻璃工業協會標準JOGIS16的規定來測定。試樣設為長度20mm±0.5mm、直徑5mm±0.5mm的圓棒，在對試樣實施98mN的負載的狀態下進行加熱，使得溫度以每分鐘4℃的恒定速度上升，每隔1秒鐘測定溫度和試樣的伸長率。平均線膨脹係數α L是在-30~70℃下的線膨脹係數的平均值。 需要說明的是，在本說明書中，以[℃ -1]的單位表示平均線膨脹係數α，但在使用[K -1]作為單位的情況下，平均線膨脹係數α的數值也相同。 The average linear expansion coefficient α L is measured based on the provisions of the Japan Optical Glass Industries Association Standard JOGIS16. The sample is set as a round bar with a length of 20 mm ± 0.5 mm and a diameter of 5 mm ± 0.5 mm. The sample is heated under a load of 98 mN so that the temperature rises at a constant rate of 4°C per minute, and the temperature and the elongation of the sample are measured every 1 second. The average linear expansion coefficient α L is the average value of the linear expansion coefficient at -30~70°C. It should be noted that in this manual, the average linear expansion coefficient α is expressed in units of [°C -1 ], but when [K -1 ] is used as the unit, the value of the average linear expansion coefficient α is the same.
＜平均線膨脹係數α 100-300＞ 在第1實施方式的光學玻璃中，在100~300℃下的平均線膨脹係數α 100-300的下限較佳為0.90×10 -5℃ -1，進一步以0.92×10 -5℃ -1、0.94×10 -5℃ -1、0.95×10 -5℃ -1的順序更佳。另外，從保持玻璃的穩定性、得到期望的光學特性的觀點考慮，平均線膨脹係數α 100-300的上限可示例出1.30×10 -5℃ -1，較佳為1.15×10 -5℃ -1，進一步以1.10×10 -5℃ -1、1.06×10 -5℃ -1、1.04×10 -5℃ -1的順序更佳。 <Average Linear Expansion Coefficient α 100-300 > In the optical glass of the first embodiment, the lower limit of the average linear expansion coefficient α 100-300 at 100 to 300°C is preferably 0.90×10 -5 °C -1 , more preferably 0.92×10 -5 °C -1 , 0.94×10 -5 °C -1 , and 0.95×10 -5 °C -1 in this order. From the viewpoint of maintaining the stability of the glass and obtaining the desired optical properties, the upper limit of the average linear expansion coefficient α 100-300 is 1.30×10 -5 ℃ -1 , preferably 1.15×10 -5 ℃ -1 , and more preferably in the order of 1.10×10 -5 ℃ -1 , 1.06×10 -5 ℃ -1 , and 1.04×10 -5 ℃ -1 .
平均線膨脹係數α 100-300基於日本光學玻璃工業協會標準JOGIS08的規定來測定。試樣設為長度20mm±0.5mm、直徑5mm±0.5mm的圓棒，在對試樣實施98mN的負載的狀態下進行加熱，使得溫度以每分鐘4℃的恆定速度上升，每隔1秒鐘測定溫度和試樣的伸長率。平均線膨脹係數α 100-300是在100~300℃下的線膨脹係數的平均值。 The average linear expansion coefficient α 100-300 is measured based on the provisions of the Japan Optical Glass Industry Association standard JOGIS08. The sample is set as a round bar with a length of 20mm±0.5mm and a diameter of 5mm±0.5mm. The sample is heated under a load of 98mN, so that the temperature rises at a constant rate of 4℃ per minute, and the temperature and the elongation of the sample are measured every 1 second. The average linear expansion coefficient α 100-300 is the average value of the linear expansion coefficient at 100~300℃.
＜相對折射率的溫度係數dn/dT＞ 對於玻璃的相對折射率的溫度係數(dn/dT)而言，藉由日本工業標準JISB7072-2(光學玻璃中的折射率的溫度係數的測定方法-第2部：干涉法)，對於波長632.8nm的光測定使溫度從-40℃變化至110℃時的相對折射率的溫度係數的值。 需要說明的是，在本說明書中，以[10 -6·℃ -1]的單位表示相對折射率的溫度係數(dn/dT)，但在使用[10 -6·K -1]作為單位的情況下，相對折射率的溫度係數dn/dT的數值也相同。 <Temperature coefficient of relative refractive index dn/dT> The temperature coefficient of relative refractive index (dn/dT) of glass is the value of the temperature coefficient of relative refractive index when the temperature is changed from -40°C to 110°C for light of wavelength 632.8nm according to Japanese Industrial Standard JIS B7072-2 (Determination of temperature coefficient of refractive index in optical glass - Part 2: Interference method). It should be noted that in this specification, the temperature coefficient of relative refractive index (dn/dT) is expressed in units of [10 -6 ·°C -1 ], but the value of the temperature coefficient of relative refractive index dn/dT is the same even when [10 -6 ·K -1 ] is used as the unit.
在第1實施方式的光學玻璃中，相對折射率的溫度係數dn/dT的上限在He-Ne雷射的波長(633nm~632.8nm)、溫度20~40℃的範圍的條件下較佳為2.0×10 -6℃ -1，進一步以1.5×10 -6℃ -1、1.0×10 -6℃ -1、0.5×10 -6℃ -1、0.0×10 -6℃ -1、-0.5×10 -6℃ -1、-1.0×10 -6℃ -1的順序更佳。另外，該相對折射率的溫度係數dn/dT的下限沒有明確的限制，在He-Ne雷射的波長(633nm~632.8nm)、且溫度20~40℃的範圍的條件下較佳為-13.0×10 -6℃ -1，進一步以-10.0×10 -6℃ -1、-9.0×10 -6℃ -1、-8.0×10 -6℃ -1、-7.0×10 -6℃ -1、-6.5×10 -6℃ -1的順序更佳。 In the optical glass of the first embodiment, the upper limit of the temperature coefficient of relative refractive index dn/dT is preferably 2.0×10 -6 ℃ -1 under the conditions of the wavelength of He-Ne laser (633nm~632.8nm) and the temperature range of 20~40℃, and is more preferably in the order of 1.5×10 -6 ℃ -1 , 1.0×10 -6 ℃ -1 , 0.5×10 -6 ℃ -1 , 0.0×10 -6 ℃ -1 , -0.5×10 -6 ℃ -1 , and -1.0×10 -6 ℃ -1 . In addition, there is no clear lower limit for the temperature coefficient of relative refractive index dn/dT. Under the conditions of the wavelength of He-Ne laser (633nm~632.8nm) and the temperature range of 20~40℃, it is preferably -13.0× 10-6 ℃ -1 , and further preferably in the order of -10.0× 10-6 ℃ -1 , -9.0× 10-6 ℃ -1 , -8.0× 10-6 ℃ -1 , -7.0× 10-6 ℃ -1 , and -6.5× 10-6 ℃ -1 .
藉由將dn/dT設為上述範圍，並將dn/dT為正的值的光學元件、或dn/dT為負的值且透鏡的焦距的符號不同的光學元件等組合，即使在光學元件的溫度大幅變動這樣的環境中，折射率的變動也變小，因此，能夠在更廣泛的溫度範圍中以高精度發揮期望的光學特性。By setting dn/dT to the above range and combining an optical element with a positive dn/dT value or an optical element with a negative dn/dT value and a lens with a different sign of focal length, the change in refractive index becomes smaller even in an environment where the temperature of the optical element changes significantly, thereby being able to exhibit the desired optical characteristics with high precision over a wider temperature range.
另一方面，能量大的光、例如雷射這樣的光、與玻璃的吸收波長相當的光等入射至玻璃時，玻璃的溫度上升幅度根據光的強度、照射時間而變化。在該情況下，也要求本實施方式的玻璃單獨減小折射率的溫度變化。On the other hand, when high-energy light, such as laser light, or light having a wavelength equivalent to the absorption wavelength of glass is incident on glass, the temperature rise of the glass varies depending on the intensity of the light and the irradiation time. In this case, the glass of the present embodiment is also required to reduce the temperature change of the refractive index alone.
以He-Ne雷射的波長(633nm~632.8nm)、溫度20~40℃的範圍為例，這樣的情況下的相對折射率的溫度係數dn/dT的上限較佳為2.0×10 -6℃ -1，進一步以1.5×10 -6℃ -1、1.0×10 -6℃ -1、0.5×10 -6℃ -1、0.3×10 -6℃ -1、0.1×10 -6℃ -1的順序更佳。另外，該相對折射率的溫度係數dn/dT的下限較佳為-2.0×10 -6℃ -1，進一步以-1.5×10 -6℃ -1、-1.0×10 -6℃ -1、-0.5×10 -6℃ -1、-0.3×10 -6℃ -1、-0.1×10 -6℃ -1的順序更佳。也可以將相對折射率的溫度係數dn/dT設為0.0×10 -6℃ -1。需要說明的是，本實施方式的光學玻璃的相對折射率的溫度係數(dn/dT)的值可以參考本說明書的記載，根據使用的雷射波長而在上述的較佳範圍中適當選擇。 Taking the wavelength of He-Ne laser (633nm~632.8nm) and the temperature range of 20~40℃ as an example, the upper limit of the temperature coefficient of relative refractive index dn/dT in this case is preferably 2.0× 10-6 ℃ -1 , and more preferably in the order of 1.5× 10-6 ℃ -1 , 1.0× 10-6 ℃ -1 , 0.5× 10-6 ℃ -1 , 0.3× 10-6 ℃ -1 , and 0.1× 10-6 ℃ -1 . In addition, the lower limit of the temperature coefficient of relative refractive index dn/dT is preferably -2.0× 10-6 °C -1 , and more preferably in the order of -1.5× 10-6 °C -1 , -1.0× 10-6 °C -1 , -0.5× 10-6 °C -1 , -0.3× 10-6 °C -1 , and -0.1× 10-6 °C -1 . The temperature coefficient of relative refractive index dn/dT may also be set to 0.0× 10-6 °C -1 . It should be noted that the value of the temperature coefficient of relative refractive index (dn/dT) of the optical glass of the present embodiment can be appropriately selected within the above-mentioned preferred range according to the laser wavelength used, with reference to the description of this specification.
＜相對折射率的溫度係數dn/dT的溫度依賴性的測定方法＞ 本實施方式的玻璃的相對折射率的溫度係數(dn/dT)的溫度依賴性小，其測定方法如下所述。 <Method for measuring temperature dependence of temperature coefficient of relative refractive index dn/dT> The temperature dependence of the temperature coefficient of relative refractive index (dn/dT) of the glass of this embodiment is small, and the method for measuring it is as follows.
相對折射率的溫度係數(dn/dT)藉由日本工業標準JISB7072-2(光學玻璃中的折射率的溫度係數的測定方法-第2部：干涉法)來測定。使溫度從-40℃變化至80℃，在溫度-30℃、-10℃、+10℃、+30℃、+50℃、+70℃下測定波長632.8nm的dn/dT(以下記載為dn/dT＠632.8)，藉由最小平方法求出dn/dT＠632.8的值相對於溫度的近似直線，將該直線的斜率設為a，將溫度0℃下的截距設為b。The temperature coefficient of relative refractive index (dn/dT) is measured according to Japanese Industrial Standard JIS B7072-2 (Determination of the temperature coefficient of refractive index in optical glass - Part 2: Interference method). The temperature is changed from -40°C to 80°C, and dn/dT at a wavelength of 632.8nm is measured at -30°C, -10°C, +10°C, +30°C, +50°C, and +70°C (hereinafter referred to as dn/dT@632.8). The approximate straight line of the value of dn/dT@632.8 with respect to temperature is obtained by the least square method, and the slope of the straight line is set as a, and the intercept at a temperature of 0°C is set as b.
上述的斜率a越接近0，基於溫度的dn/dT的變化量越小，因此，意味著在不同的溫度範圍中，隨著溫度變化的dn/dT值的變化也越小。也就是說，光學元件的焦距相對於單位溫度變化的偏移是恆定的，與溫度無關，因此，能夠使受光元件側的位置調整構造簡化，對於要求高精度的成像的光學元件是有效的。The closer the slope a is to 0, the smaller the change in dn/dT due to temperature. Therefore, it means that the change in dn/dT value due to temperature change is also smaller in different temperature ranges. In other words, the offset of the focal length of the optical element relative to the unit temperature change is constant and has nothing to do with the temperature. Therefore, the position adjustment structure on the light-receiving element side can be simplified, which is effective for optical elements that require high-precision imaging.
因此，在本實施方式的光學玻璃中，上述斜率a的值的範圍較佳為10.0×10 -9~-10.0×10 -9，進一步以8.0×10 -9~-8.0×10 -9、6.0×10 -9~-6.0×10 -9、4.0×10 -9~-4.0×10 -9、3.0×10 -9~-3.0×10 -9的順序更佳。 Therefore, in the optical glass of the present embodiment, the value of the slope a is preferably in the range of 10.0×10 -9 to -10.0×10 -9 , and more preferably in the order of 8.0×10 -9 to -8.0×10 -9 , 6.0×10 -9 to -6.0×10 -9 , 4.0×10 -9 to -4.0×10 -9 , and 3.0×10 -9 to -3.0×10 -9 .
另外，上述的截距b越接近0.0×10 -6，近似直線中的0℃下的dn/dT＠632.8的值越小，因此，意味著dn/dT的值的絕對值越小。因此，單獨的光學元件的焦距相對於單位溫度變化的偏移量本身小，因此，對於要求高精度的成像的光學元件是有效的。 In addition, the closer the intercept b is to 0.0×10 -6 , the smaller the value of dn/dT@632.8 at 0°C in the approximate straight line is, which means that the absolute value of dn/dT is smaller. Therefore, the amount of deviation of the focal length of a single optical element relative to a unit temperature change is small, and it is effective for optical elements that require high-precision imaging.
因此，在本實施方式的光學玻璃中，上述截距b的值的範圍較佳為3.0×10 -6~-3.0×10 -6，進一步以2.0×10 -6~-2.0×10 -6、1.0×10 -6~-1.0×10 -6、0.5×10 -6~-0.5×10 -6的順序更佳。需要說明的是，如果將上述斜率a的值控制為一定的值以下、較佳控制為0附近，則上述截距b也可以不一定為0。也可以將上述截距b設為0附近。 Therefore, in the optical glass of the present embodiment, the intercept b is preferably in the range of 3.0×10 -6 to -3.0×10 -6 , and more preferably in the order of 2.0×10 -6 to -2.0×10 -6 , 1.0×10 -6 to -1.0×10 -6 , and 0.5×10 -6 to -0.5×10 -6 . It should be noted that if the slope a is controlled to a certain value or less, preferably to be near 0, the intercept b may not necessarily be 0. The intercept b may also be set to be near 0.
＜玻璃化轉變溫度Tg＞ 第1實施方式的光學玻璃的玻璃化轉變溫度Tg的上限較佳為730℃，進一步以720℃、710℃、700℃的順序更佳。另外，玻璃化轉變溫度Tg的下限較佳為500℃，進一步以550℃、560℃、570℃、580℃的順序更佳。 <Glass transition temperature Tg> The upper limit of the glass transition temperature Tg of the optical glass of the first embodiment is preferably 730°C, and more preferably in the order of 720°C, 710°C, and 700°C. In addition, the lower limit of the glass transition temperature Tg is preferably 500°C, and more preferably in the order of 550°C, 560°C, 570°C, and 580°C.
藉由使玻璃化轉變溫度Tg的上限滿足上述範圍，能夠抑制玻璃的成型溫度及退火溫度的上升，能夠減輕對壓製成型用設備及退火設備的熱損傷。另外，藉由使玻璃化轉變溫度Tg的下限滿足上述範圍，容易保持期望的阿貝數、折射率，並且良好地保持玻璃的熱穩定性。另外，在用作精密壓製原材料時能夠得到良好的成型性。By making the upper limit of the glass transition temperature Tg satisfy the above range, the increase in the molding temperature and annealing temperature of the glass can be suppressed, and the thermal damage to the press molding equipment and annealing equipment can be reduced. In addition, by making the lower limit of the glass transition temperature Tg satisfy the above range, it is easy to maintain the desired Abbe number and refractive index, and the thermal stability of the glass can be well maintained. In addition, good moldability can be obtained when used as a precision pressing raw material.
另一方面，存在玻璃化轉變溫度Tg越高、隨著單位溫度變化的膨脹量越小的傾向，因此，存在能夠減輕由隨著單位溫度變化的熱膨脹導致的形狀變化程度的傾向。另外，藉由加熱，玻璃的溫度上升至Tg附近或應變點以上時，存在即使之後玻璃被冷卻、光學性能也無法恢復至原來的狀態之虞。因此，Tg的下限較佳滿足上述範圍。On the other hand, the higher the glass transition temperature Tg, the smaller the amount of expansion per unit temperature change tends to be, so the degree of shape change caused by thermal expansion per unit temperature change tends to be reduced. In addition, when the temperature of the glass rises to near Tg or above the strain point by heating, there is a possibility that the optical performance may not be restored to the original state even if the glass is cooled later. Therefore, the lower limit of Tg preferably satisfies the above range.
＜玻璃的比重＞ 在第1實施方式的光學玻璃中，其比重較佳為5.50以下，進一步以5.00以下、4.80以下的順序更佳。如果能夠降低玻璃的比重，則能夠減少透鏡的重量。其結果是，能夠減少搭載透鏡的相機透鏡的自動聚焦驅動的消耗功率。 <Specific gravity of glass> In the optical glass of the first embodiment, the specific gravity is preferably 5.50 or less, and more preferably 5.00 or less, and 4.80 or less. If the specific gravity of the glass can be reduced, the weight of the lens can be reduced. As a result, the power consumption of the autofocus drive of the camera lens equipped with the lens can be reduced.
＜玻璃的光線透射性＞ 第1實施方式的光學玻璃的光線透射性可以藉由著色度λ5、λ70及λ80來評價。 對於厚度10.0mm±0.1mm的玻璃試樣，在波長200~700nm的範圍測定分光透射率，將外部透射率達到5%的波長設為λ5、將外部透射率達到70%的波長設為λ70、將外部透射率達到80%的波長設為λ80。 <Light transmittance of glass> The light transmittance of the optical glass of the first embodiment can be evaluated by chromaticity λ5, λ70, and λ80. For a glass sample with a thickness of 10.0 mm ± 0.1 mm, the spectral transmittance is measured in the wavelength range of 200 to 700 nm, and the wavelength at which the external transmittance reaches 5% is set as λ5, the wavelength at which the external transmittance reaches 70% is set as λ70, and the wavelength at which the external transmittance reaches 80% is set as λ80.
第1實施方式的光學玻璃的λ5較佳為400nm以下，更佳較佳為380nm以下，進一步較佳為360nm以下，特別較佳為350nm以下。The λ5 of the optical glass according to the first embodiment is preferably 400 nm or less, more preferably 380 nm or less, further preferably 360 nm or less, and particularly preferably 350 nm or less.
第1實施方式的光學玻璃的λ70較佳為440nm以下，更佳較佳為430nm以下，進一步較佳為420nm以下。The λ70 of the optical glass according to the first embodiment is preferably 440 nm or less, more preferably 430 nm or less, and further preferably 420 nm or less.
第1實施方式的光學玻璃的λ80較佳為510nm以下，更佳較佳為500nm以下，進一步較佳為490nm以下。The λ80 of the optical glass according to the first embodiment is preferably 510 nm or less, more preferably 500 nm or less, and further preferably 490 nm or less.
藉由使用λ5、λ70及λ80如上述那樣地被短波長化的光學玻璃，可以提供能夠實現適宜的顏色再現的光學元件。By using optical glass whose wavelengths are shortened as described above, such as λ5, λ70, and λ80, an optical element capable of achieving appropriate color reproduction can be provided.
(光學玻璃的製造) 以成為上述給定的組成的方式調配玻璃原料，藉由調配的玻璃原料並按照已知的玻璃製造方法製作本發明的實施方式的光學玻璃即可。例如，調配多種化合物，充分混合而制成批原料，將批原料加入石英坩堝、鉑坩堝中，進行粗熔解(rough melt)，對藉由粗熔解得到的熔融物進行驟冷、粉碎而製作碎玻璃，進一步將碎玻璃加入鉑坩堝中，進行加熱、再熔融(remelt)而製成熔融玻璃，進一步進行澄清、均勻化後，將熔融玻璃成型，緩慢冷卻而得到光學玻璃。熔融玻璃的成型、緩慢冷卻應用已知的方法即可。 (Manufacturing of optical glass) Glass raw materials are prepared in a manner to form the above-mentioned given composition, and the optical glass of the embodiment of the present invention can be manufactured by the prepared glass raw materials and according to the known glass manufacturing method. For example, a plurality of compounds are prepared and fully mixed to form a batch raw material, the batch raw material is added to a quartz crucible or a platinum crucible, and the rough melt is performed, and the molten material obtained by the rough melt is quenched and crushed to produce cullet, and the cullet is further added to a platinum crucible, heated, and remelted to produce molten glass, and after further clarification and homogenization, the molten glass is molded and slowly cooled to obtain optical glass. The molding and slow cooling of the molten glass can be applied by known methods.
需要說明的是，只要能夠以成為期望的含量的方式在玻璃中導入期望的玻璃成分，則調配批原料時使用的化合物沒有特別限定，作為這樣的化合物，可舉出氧化物、碳酸鹽、硝酸鹽、氫氧化物、氟化物等。It should be noted that as long as the desired glass components can be introduced into the glass in the desired content, the compounds used when preparing the batch raw materials are not particularly limited, and examples of such compounds include oxides, carbonates, nitrates, hydroxides, fluorides, and the like.
(光學元件等的製造) 使用本發明的實施方式的光學玻璃製作光學元件應用已知的方法即可。例如，將玻璃原料熔融而製成熔融玻璃，將該熔融玻璃注入鑄模而成型為板狀，製作由本發明的光學玻璃形成的玻璃原材料。對得到的玻璃原材料適當進行切割、磨削、拋光，製作適於壓製成型的大小、形狀的碎片。對碎片進行加熱、軟化，藉由已知的方法進行壓製成型(再熱壓)，製作近似於光學元件的形狀的光學元件毛坯。對光學元件毛坯進行退火，藉由已知的方法進行磨削、拋光，製作光學元件。 (Manufacturing of optical elements, etc.) Known methods can be applied to manufacturing optical elements using the optical glass of the embodiment of the present invention. For example, glass raw materials are melted to make molten glass, and the molten glass is poured into a casting mold to be formed into a plate to manufacture glass raw materials formed by the optical glass of the present invention. The obtained glass raw materials are appropriately cut, ground, and polished to produce fragments of a size and shape suitable for press molding. The fragments are heated and softened, and press molded (re-hot pressing) by a known method to produce an optical element blank of a shape similar to that of an optical element. The optical element blank is annealed, and ground and polished by a known method to manufacture an optical element.
根據使用目的，可以在製作的光學元件的光學功能面包覆防反射膜、全反射膜等。Depending on the purpose of use, the optical functional surface of the manufactured optical element can be coated with an anti-reflection film, a total reflection film, etc.
作為光學元件，可示例出球面透鏡等各種透鏡、稜鏡、繞射光柵等。Examples of the optical element include various lenses such as a spherical lens, a prism, a diffraction grating, and the like.
以下，對第2實施方式詳細地進行說明。The second implementation method is described in detail below.
第2實施方式 第2實施方式的光學玻璃如下：以陽離子%表示， B 3+的含量與B 3+及Si 4+的合計含量的陽離子比[B 3+/(B 3++Si 4+)]為1/3以上， Ba 2+及Sr 2+的合計含量與Li +、Na +、K +、Cs +、Mg 2+、Ca 2+、Sr 2+及Ba 2+的合計含量的陽離子比[(Ba 2++Sr 2+)/(Li ++Na ++K ++Cs ++Mg 2++Ca 2++Sr 2++Ba 2+)]為0.62以上， Ba 2+及Li +的合計含量與Na +、K +、Si 4+、Ti 4+、Nb 5+及W 6+的合計含量的陽離子比[(Ba 2++Li +)/(Na ++K ++Si 4++Ti 4++Nb 5++W 6+)]為8/9以上， Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+及Zr 4+的合計含量[Gd 3++Zn 2++Ti 4++Nb 5++W 6++Zr 4+]為13.00陽離子%以下， La 3+、Y 3+、Ba 2+、Li +的合計含量[La 3++Y 3++Ba 2++Li +]為36陽離子%以上， La 3+、Gd 3+及Y 3+的合計含量與B 3+的含量、Si 4+的含量的2倍、Al 3+的含量的合計的陽離子比[(La 3++Gd 3++Y 3+)/{B 3++(2×Si 4+)+Al 3+}]為0.360以上。 Second embodiment The optical glass of the second embodiment is as follows: expressed in terms of cation %, the cation ratio of the content of B 3+ to the total content of B 3+ and Si 4+ [B 3+ /(B 3+ +Si 4+ )] is 1/3 or more, the cation ratio of the total content of Ba 2+ and Sr 2+ to the total content of Li + , Na + , K + , Cs + , Mg 2+ , Ca 2+ , Sr 2+ and Ba 2+ [(Ba 2+ +Sr 2+ )/(Li + +Na + +K + +Cs + +Mg 2+ +Ca 2+ +Sr 2+ +Ba 2+ )] is 0.62 or more, the total content of Ba 2+ and Li + to the total content of Na + , K + , Si 4+ , Ti 4+ , Nb 5+ and W The cation ratio of the total content of Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ [(Ba 2+ +Li + )/(Na + +K + +Si 4+ +Ti 4+ +Nb 5+ +W 6+ )] is 8/9 or more, the total content of Gd 3+ , Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ [Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Zr 4+ ] is 13.00 cation % or less, the total content of La 3+ , Y 3+ , Ba 2+ and Li + [La 3+ +Y 3+ +Ba 2+ +Li + ] is 36 cation % or more, the total content of La 3+ , Gd 3+ and Y 3+ and the content of B 3+ , Si 4+ are 2.5 cation % or less, and the total content of Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ are 2.5 cation % or less. The total cation ratio of twice the content of Si 4+ and the content of Al 3+ [(La 3+ +Gd 3+ +Y 3+ )/{B 3+ +(2×Si 4+ )+Al 3+ }] is 0.360 or more.
在第2實施方式中，B 3+的含量與B 3+及Si 4+的合計含量的陽離子比[B 3+/(B 3++Si 4+)]為1/3以上。該陽離子比的下限較佳為1.1/3，進一步以1.2/3、1.3/3、1.4/3、1.5/3、1.6/3、1.7/3、1.8/3、1.9/3的順序更佳。另外，該陽離子比的上限較佳為3.0/3，進一步以2.9/3、2.8/3、2.7/3、2.6/3、2.5/3、2.4/3、2.3/3的順序更佳。 In the second embodiment, the cation ratio of the content of B 3+ to the total content of B 3+ and Si 4+ [B 3+ /(B 3+ +Si 4+ )] is 1/3 or more. The lower limit of the cation ratio is preferably 1.1/3, and more preferably in the order of 1.2/3, 1.3/3, 1.4/3, 1.5/3, 1.6/3, 1.7/3, 1.8/3, and 1.9/3. In addition, the upper limit of the cation ratio is preferably 3.0/3, and more preferably in the order of 2.9/3, 2.8/3, 2.7/3, 2.6/3, 2.5/3, 2.4/3, and 2.3/3.
藉由將陽離子比[B 3+/(B 3++Si 4+)]設為上述範圍，能夠得到在-30~70℃下的平均線膨脹係數α L大的低色散的光學玻璃。另外，能夠降低玻璃的相對折射率的溫度係數(dn/dT)。此外，即使在大量含有La 3+的情況下，也能夠抑制玻璃的熱穩定性的降低。另一方面，該陽離子比過小時，在大量包含作為提高折射率nd、防止平均線膨脹係數α L的降低的玻璃成分的La 3+及Y 3+的情況下，存在玻璃變得不穩定之虞。另外，該陽離子比過大時，存在玻璃的穩定性、化學耐久性及機械特性降低之虞。 By setting the cation ratio [B 3+ /(B 3+ +Si 4+ )] to the above range, a low-dispersion optical glass having a large average linear expansion coefficient α L at -30 to 70°C can be obtained. In addition, the temperature coefficient (dn/dT) of the relative refractive index of the glass can be reduced. In addition, even when La 3+ is contained in a large amount, the reduction in thermal stability of the glass can be suppressed. On the other hand, when the cation ratio is too small, there is a risk that the glass will become unstable when La 3+ and Y 3+ are contained in large amounts as glass components that increase the refractive index nd and prevent the reduction in the average linear expansion coefficient α L. In addition, when the cation ratio is too large, there is a risk that the stability, chemical durability and mechanical properties of the glass will be reduced.
在第2實施方式中，Ba 2+及Sr 2+的合計含量與Li +、Na +、K +、Cs +、Mg 2+、Ca 2+、Sr 2+及Ba 2+的合計含量的陽離子比[(Ba 2++Sr 2+)/(Li ++Na ++K ++Cs ++Mg 2++Ca 2++Sr 2++Ba 2+)]為0.62以上。該陽離子比的下限較佳為0.63，進一步以0.65、0.67、0.69、0.71、0.73、0.75、0.77、0.79、0.81、0.83、0.85、0.87的順序更佳。另外，該陽離子比的上限較佳為1.00，進一步以0.99、0.98的順序更佳。該陽離子比也可以為1.00。 In the second embodiment, the cation ratio of the total content of Ba2 + and Sr2 + to the total content of Li + , Na + , K + , Cs + , Mg2 + , Ca2 + , Sr2 + and Ba2 + [( Ba2 + + Sr2+ )/(Li + +Na + +K + +Cs + + Mg2 + + Ca2 + + Sr2 + +Ba2 + )] is 0.62 or more. The lower limit of the cation ratio is preferably 0.63, and more preferably in the order of 0.65, 0.67, 0.69, 0.71, 0.73, 0.75, 0.77, 0.79, 0.81, 0.83, 0.85, and 0.87. The upper limit of the cation ratio is preferably 1.00, more preferably in the order of 0.99 and 0.98. The cation ratio may also be 1.00.
藉由將陽離子比[(Ba 2++Sr 2+)/(Li ++Na ++K ++Cs ++Mg 2++Ca 2++Sr 2++Ba 2+)]設為上述範圍，可得到平均線膨脹係數α L大的高折射率的光學玻璃。另外，能夠增大平均線膨脹係數α L，並且抑制熱穩定性的降低。另一方面，該陽離子比過小時，存在平均線膨脹係數α L及折射率nd降低、玻璃的穩定性受損之虞。 By setting the cation ratio [(Ba 2+ +Sr 2+ )/(Li + +Na + +K + +Cs + + Mg 2+ +Ca 2+ +Sr 2+ +Ba 2+ )] within the above range, an optical glass having a large average linear expansion coefficient α L and a high refractive index can be obtained. In addition, the average linear expansion coefficient α L can be increased and a decrease in thermal stability can be suppressed. On the other hand, when the cation ratio is too small, there is a risk that the average linear expansion coefficient α L and the refractive index nd will decrease, and the stability of the glass may be impaired.
在第2實施方式中，Ba 2+及Li +的合計含量與Na +、K +、Si 4+、Ti 4+、Nb 5+及W 6+的合計含量的陽離子比[(Ba 2++Li +)/(Na ++K ++Si 4++Ti 4++Nb 5++W 6+)]為8/9以上。該陽離子比的下限較佳為8.2/9，進一步以8.4/9、8.6/9、8.8/9、9.0/9、9.2/9、9.4/9、9.5/9的順序更佳。另外，該陽離子比的上限較佳為27/9，進一步以25/9、23/9、21/9、19/9、17/9、15/9、13/9、12/9的順序更佳。 In the second embodiment, the cation ratio of the total content of Ba 2+ and Li + to the total content of Na + , K + , Si 4+ , Ti 4+ , Nb 5+ and W 6+ [(Ba 2+ +Li + )/(Na + +K + +Si 4+ +Ti 4+ +Nb 5+ +W 6+ )] is 8/9 or more. The lower limit of the cation ratio is preferably 8.2/9, and more preferably in the order of 8.4/9, 8.6/9, 8.8/9, 9.0/9, 9.2/9, 9.4/9, and 9.5/9. In addition, the upper limit of the cation ratio is preferably 27/9, and more preferably in the order of 25/9, 23/9, 21/9, 19/9, 17/9, 15/9, 13/9, and 12/9.
藉由將陽離子比[(Ba 2++Li +)/(Na ++K ++Si 4++Ti 4++Nb 5++W 6+)]設為上述範圍，可得到平均線膨脹係數α L大的高折射率低色散性的光學玻璃。另外，能夠降低玻璃的相對折射率的溫度係數(dn/dT)。另一方面，該陽離子比過小時，存在平均線膨脹係數α L降低、玻璃的高折射低色散性喪失之虞。另外，該陽離子比過大時，存在玻璃的穩定性降低之虞。 By setting the cation ratio [(Ba 2+ +Li + )/(Na + +K + +Si 4+ +Ti 4+ +Nb 5+ +W 6+ )] to the above range, a high refractive index and low dispersion optical glass with a large average linear expansion coefficient α L can be obtained. In addition, the temperature coefficient of the relative refractive index of the glass (dn/dT) can be reduced. On the other hand, when the cation ratio is too small, there is a risk that the average linear expansion coefficient α L is reduced and the high refractive index and low dispersion of the glass are lost. In addition, when the cation ratio is too large, there is a risk that the stability of the glass is reduced.
在第2實施方式中，Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+及Zr 4+的合計含量[Gd 3++Zn 2++Ti 4++Nb 5++W 6++Zr 4+]為13.00%以下。該合計含量的上限較佳為12.50%，進一步以12.00%、11.50%、11.00%、10.50%、10.00%、9.50%、9.00%的順序更佳。另外，該合計含量的下限較佳為0%，進一步以1.00%、2.00%、3.00%、4.00%、5.00%、6.00%、7.00%、8.00%的順序更佳。該合計含量可以為0。 In the second embodiment, the total content of Gd 3+ , Zn 2+ , Ti 4+ , Nb 5+ , W 6+ and Zr 4+ [Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Zr 4+ ] is 13.00% or less. The upper limit of the total content is preferably 12.50%, and more preferably in the order of 12.00%, 11.50%, 11.00%, 10.50%, 10.00%, 9.50%, and 9.00%. In addition, the lower limit of the total content is preferably 0%, and more preferably in the order of 1.00%, 2.00%, 3.00%, 4.00%, 5.00%, 6.00%, 7.00%, and 8.00%. The total content may be 0.
藉由將合計含量[Gd 3++Zn 2++Ti 4++Nb 5++W 6++Zr 4+]設為上述範圍，可藉由抑制平均線膨脹係數α L的降低、並且抑制高色散化而得到高折射率低色散性的光學玻璃。此外，還具有不增大玻璃的相對折射率的溫度係數(dn/dT)的效果。該合計含量可以為0，但為了調整阿貝數νd等光學常數，也可以將該合計含量設為大於0。另一方面，該合計含量過大時，存在平均線膨脹係數α L降低、並且玻璃的高折射低色散性損失之虞。 By setting the total content [Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Zr 4+ ] to the above range, an optical glass with high refractive index and low dispersion can be obtained by suppressing the decrease of the average linear expansion coefficient α L and suppressing high dispersion. In addition, it also has the effect of not increasing the temperature coefficient (dn/dT) of the relative refractive index of the glass. The total content can be 0, but in order to adjust the optical constants such as the Abbe number νd, the total content can also be set to greater than 0. On the other hand, when the total content is too large, there is a risk that the average linear expansion coefficient α L is reduced and the high refractive index and low dispersion of the glass are lost.
在第2實施方式中，La 3+、Y 3+、Ba 2+、Li +的合計含量[La 3++Y 3++Ba 2++Li +]為36%以上。該合計含量的下限較佳為38%，進一步以40%、41%、42%、43%、44%的順序更佳。另外，該合計含量的上限較佳為55%，進一步以54%、53%、52%、51%、50%、49%、48%、47%的順序更佳。 In the second embodiment, the total content of La 3+ , Y 3+ , Ba 2+ , and Li + [La 3+ +Y 3+ +Ba 2+ +Li + ] is 36% or more. The lower limit of the total content is preferably 38%, and more preferably in the order of 40%, 41%, 42%, 43%, and 44%. In addition, the upper limit of the total content is preferably 55%, and more preferably in the order of 54%, 53%, 52%, 51%, 50%, 49%, 48%, and 47%.
藉由將合計含量[La 3++Y 3++Ba 2++Li +]設為上述範圍，可得到抑制了平均線膨脹係數α L的降低、並且高折射率低色散性的光學玻璃。另外，還具有不增大玻璃的相對折射率的溫度係數(dn/dT)的效果。另一方面，該合計含量過小時，存在平均線膨脹係數α L降低、玻璃的高折射低色散性損失之虞。另外，該合計含量過大時，存在玻璃的熱穩定性降低之虞。 By setting the total content [La 3+ +Y 3+ +Ba 2+ +Li + ] to the above range, an optical glass having a high refractive index and low dispersion while suppressing the decrease in the average linear expansion coefficient α L can be obtained. In addition, there is an effect of not increasing the temperature coefficient of the relative refractive index (dn/dT) of the glass. On the other hand, when the total content is too small, there is a risk that the average linear expansion coefficient α L is reduced and the high refractive index and low dispersion of the glass are lost. In addition, when the total content is too large, there is a risk that the thermal stability of the glass is reduced.
在第2實施方式中，La 3+、Gd 3+及Y 3+的合計含量與B 3+的含量、Si 4+的含量的2倍、Al 3+的含量的合計的陽離子比[(La 3++Gd 3++Y 3+)/{B 3++(2×Si 4+)+Al 3+}]為0.360以上。該陽離子比的下限較佳為0.370，進一步以0.380、0.390、0.400、0.410、0.420、0.425的順序更佳。特別是，為了兼顧平均線膨脹係數α L的增大和高折射低色散，上述值的下限較佳為0.440、0.450、0.460、0.470、0.480。另外，該陽離子比的上限較佳為0.550，進一步以0.540、0.530、0.520、0.510、0.500、0.490的順序更佳。 In the second embodiment, the cation ratio of the total content of La 3+ , Gd 3+ and Y 3+ to the content of B 3+ , twice the content of Si 4+ , and the content of Al 3+ [(La 3+ +Gd 3+ +Y 3+ )/{B 3+ +(2×Si 4+ )+Al 3+ }] is 0.360 or more. The lower limit of the cation ratio is preferably 0.370, and more preferably in the order of 0.380, 0.390, 0.400, 0.410, 0.420, and 0.425. In particular, in order to take into account both the increase in the average linear expansion coefficient α L and the high refractive index and low dispersion, the lower limit of the above value is preferably 0.440, 0.450, 0.460, 0.470, and 0.480. In addition, the upper limit of the cation ratio is preferably 0.550, and further preferably in the order of 0.540, 0.530, 0.520, 0.510, 0.500, and 0.490.
藉由將陽離子比[(La 3++Gd 3++Y 3+)/{B 3++(2×Si 4+)+Al 3+}設為上述範圍，可得到能夠在確保玻璃的穩定性的同時將折射率的降低抑制為最小限度的高折射率低色散的光學玻璃。另一方面，該陽離子比過大時，存在玻璃的熱穩定性降低之虞。 By setting the cation ratio [(La 3+ +Gd 3+ +Y 3+ )/{B 3+ +(2×Si 4+ )+Al 3+ }] within the above range, a high refractive index, low dispersion optical glass can be obtained that can minimize the decrease in refractive index while ensuring the stability of the glass. On the other hand, if the cation ratio is too large, there is a risk that the thermal stability of the glass will be reduced.
在第2實施方式中，Gd 3+、Zn 2+、Ti 4+、Nb 5+、W 6+、Bi 3+的合計含量與Y 3+的含量的陽離子比[(Gd 3++Zn 2++Ti 4++Nb 5++W 6++Bi 3+)/Y 3+]的上限較佳為2.0，進一步以1.8、1.6、1.4、1.2、1.1、1.0、0.9、0.8、0.6的順序更佳。另外，該陽離子比的下限較佳為0，進一步以0.1、0.2、0.3、0.4的順序更佳。該陽離子比可以為0。 In the second embodiment, the upper limit of the cation ratio of the total content of Gd 3+ , Zn 2+ , Ti 4+ , Nb 5+ , W 6+ , and Bi 3+ to the content of Y 3+ [(Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Bi 3+ )/Y 3+ ] is preferably 2.0, and more preferably in the order of 1.8, 1.6, 1.4, 1.2, 1.1, 1.0, 0.9, 0.8, and 0.6. In addition, the lower limit of the cation ratio is preferably 0, and more preferably in the order of 0.1, 0.2, 0.3, and 0.4. The cation ratio may be 0.
從提高平均線膨脹係數α L、抑制玻璃的熱穩定性的降低的觀點考慮，陽離子比[(Gd 3++Zn 2++Ti 4++Nb 5++W 6++Bi 3+)/Y 3+]較佳設為上述範圍。該陽離子比可以為0，但為了調整阿貝數νd等光學常數，也可以使該陽離子比大於0。另一方面，該陽離子比過大時，存在平均線膨脹係數α L降低、並且玻璃的高折射低色散性喪失之虞。 From the viewpoint of increasing the average linear expansion coefficient α L and suppressing the decrease in the thermal stability of the glass, the cation ratio [(Gd 3+ +Zn 2+ +Ti 4+ +Nb 5+ +W 6+ +Bi 3+ )/Y 3+ ] is preferably set to the above range. The cation ratio may be 0, but in order to adjust optical constants such as the Abbe number νd, the cation ratio may be greater than 0. On the other hand, when the cation ratio is too large, there is a risk that the average linear expansion coefficient α L decreases and the high refractive and low dispersion properties of the glass are lost.
在第2實施方式的光學玻璃中，可以將上述以外的玻璃成分的含量及比率設為與第1實施方式同樣。In the optical glass of the second embodiment, the contents and ratios of the glass components other than those described above can be the same as those of the first embodiment.
在第2實施方式的光學玻璃中，可以將玻璃特性也設為與第1實施方式同樣。In the optical glass of the second embodiment, the glass properties can also be set to be the same as those of the first embodiment.
可以將第2實施方式的光學玻璃的製造及光學元件等的製造設為與第1實施方式同樣。The production of the optical glass and the production of the optical elements, etc., of the second embodiment can be made the same as those of the first embodiment.
以下，對第3實施方式詳細地進行說明。The third embodiment is described in detail below.
第3實施方式 第3實施方式的光學玻璃如下：以氧化物基準計，將玻璃成分SiO 2、B 2O 3、Al 2O 3、Li 2O、Na 2O、K 2O、Cs 2O、MgO、CaO、SrO、BaO、ZnO、La 2O 3、Gd 2O 3、Y 2O 3、ZrO 2、TiO 2、Nb 2O 5、WO 3及Bi 2O 3的以質量%表示的含量分別設為C(SiO 2)、C(B 2O 3)、C(Al 2O 3)、C(Li 2O)、C(Na 2O)、C(K 2O)、C(Cs 2O)、C(MgO)、C(CaO)、C(SrO)、C(BaO)、C(ZnO)、C(La 2O 3)、C(Gd 2O 3)、C(Y 2O 3)、C(ZrO 2)、C(TiO 2)、C(Nb 2O 5)、C(WO 3)及C(Bi 2O 3)， 將SiO 2、BO 1.5、AlO 1.5、LiO 0.5、NaO 0.5、KO 0.5、CsO 0.5、MgO、CaO、SrO、BaO、ZnO、LaO 1.5、GdO 1.5、YO 1.5、ZrO 2、TiO 2、NbO 2.5、WO 3及BiO 1.5的各化學式量分別設為M(SiO 2)、M(BO 1.5)、M(AlO 1.5)、M(LiO 0.5)、M(NaO 0.5)、M(KO 0.5)、M(CsO 0.5)、M(MgO)、M(CaO)、M(SrO)、M(BaO)、M(ZnO)、M(LaO 1.5)、M(GdO 1.5)、M(YO 1.5)、M(ZrO 2)、M(TiO 2)、M(NbO 2.5)、M(WO 3)及M(BiO 1.5)， 並且設定： A1＝{C(B 2O 3)/M(BO 1.5)}/{C(B 2O 3)/M(BO 1.5)+C(SiO 2)/M(SiO 2)}、 B1＝{C(BaO)/M(BaO)+C(SrO)/M(SrO)}/{C(Li 2O)/M(LiO 0.5)+C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(Cs 2O)/M(CsO 0.5)+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}、 C1＝{C(BaO)/M(BaO)+C(Li 2O)/M(LiO 0.5)}/{C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(SiO 2)/M(SiO 2)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)}、 D1＝C(Gd 2O 3)+C(ZnO)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)+C(ZrO 2)、 E1＝{C(La 2O 3)+C(Gd 2O 3)+C(Y 2O 3)}/{C(SiO 2)+C(B 2O 3)+C(Al 2O 3)}、 F1＝{C(Gd 2O 3)/M(GdO 1.5)+C(ZnO)/M(ZnO)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)+C(Bi 2O 3)/M(BiO 1.5)}/{C(Y 2O 3)/M(YO 1.5)}時， A1為1/3以上， B1為0.62以上， C1為8/9以上， D1為13.50以下， E1為1.25以上， F1為2.0以下。 Third Embodiment The optical glass of the third embodiment is as follows: On an oxide basis, the contents of glass components SiO 2 , B 2 O 3 , Al 2 O 3 , Li 2 O , Na 2 O, K 2 O, Cs 2 O, MgO, CaO, SrO, BaO, ZnO, La 2 O 3 , Gd 2 O 3 , Y 2 O 3 , ZrO 2 , TiO 2 , Nb 2 O 5 , WO 3 and Bi 2 O 3, expressed in mass %, are respectively C(SiO 2 ), C(B 2 O 3 ), C(Al 2 O 3 ), C(Li 2 O ), C(Na 2 O ), C(K 2 O ), C(Cs 2 O ), C(MgO ), C(CaO ), C(SrO ), C(BaO ), C(ZnO ), C(La 2 O 3 ), C(Gd 2 O 3 ), C(Y 2 O 3 ), C(ZrO 2 ), C(TiO 2 ), C(Nb 2 O 5 ), C(WO 3 ) and C(Bi 2 O 3 ), and the chemical formula weights of SiO 2 , BO 1.5 , AlO 1.5 , LiO 0.5 , NaO 0.5 , KO 0.5 , CsO 0.5 , MgO, CaO, SrO, BaO, ZnO, LaO 1.5 , GdO 1.5 , YO 1.5 , ZrO 2 , TiO 2 , NbO 2.5 , WO 3 and BiO 1.5 are respectively designated M(SiO 2 ), M(BO 1.5 ), M(AlO 1.5 ), M(LiO 0.5 ), M(NaO 0.5 ), M(KO 0.5 ), M(CsO 0.5 ), M(MgO), M(CaO), M(SrO), M(BaO), M(ZnO), M(LaO 1.5 ), M(GdO 1.5 ), M(YO 1.5 ), M(ZrO 2 ), M(TiO 2 ), M(NbO 2.5 ) , M(WO 3 ) and M(BiO 1.5 ), and set: A1={C(B 2 O 3 )/M(BO 1.5 )}/{C(B 2 O 3 )/M(BO 1.5 )+C(SiO 2 )/M(SiO 2 )}, B1={C(BaO)/M(BaO)+C(SrO)/M(SrO)}/{C(Li 2 O)/M(LiO 0.5 )+C(Na 2 O)/M(NaO 0.5 )+C(K 2 O)/M(KO 0.5 )+C(Cs 2 O)/M(CsO 0.5 )+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}, C1={C(BaO)/M(BaO)+C(Li 2 O)/M(LiO 0.5 )}/{C(Na 2 O)/M(NaO 0.5 )+C(K 2 O)/M(KO 0.5 )+C(SiO 2 )/M(SiO 2 )+C(TiO 2 )/M(TiO 2 )+C(Nb 2 O 5 )/M(NbO 2.5 )+C(WO 3 )/M(WO 3 )}, D1=C(Gd 2 O 3 )+C(ZnO)+C(TiO 2 )+C(Nb 2 O 5 )+C(WO 3 )+C(ZrO 2 ), E1={C(La 2 O 3 )+C(Gd 2 O 3 )+C(Y 2 O 3 )}/{C( SiO 2 )+C(B 2 O 3 )+C(Al 2 O 3 )}, F1={C(Gd 2 O 3 )/M(GdO 1.5 )+C(ZnO)/M(ZnO)+C(TiO 2 )/M(TiO 2 )+C(Nb 2 O 5 )/M(NbO 2.5 )+C(WO 3 )/M(WO 3 )+C(Bi 2 O 3 )/M(BiO 1.5 )}/{C(Y 2 O 3 )/M(YO 1.5 )}, A1 is 1/3 or more, B1 is 0.62 or more, C1 is 8/9 or more, D1 is 13.50 or less, E1 is 1.25 or more, and F1 is 2.0 or less.
在第3實施方式中，以氧化物基準計，將玻璃成分SiO 2、B 2O 3、Al 2O 3、Li 2O、Na 2O、K 2O、Cs 2O、MgO、CaO、SrO、BaO、ZnO、La 2O 3、Gd 2O 3、Y 2O 3、ZrO 2、TiO 2、Nb 2O 5、WO 3及Bi 2O 3的以質量%表示的含量分別設為C(SiO 2)、C(B 2O 3)、C(Al 2O 3)、C(Li 2O)、C(Na 2O)、C(K 2O)、C(Cs 2O)、C(MgO)、C(CaO)、C(SrO)、C(BaO)、C(ZnO)、C(La 2O 3)、C(Gd 2O 3)、C(Y 2O 3)、C(ZrO 2)、C(TiO 2)、C(Nb 2O 5)、C(WO 3)及C(Bi 2O 3)。 In the third embodiment, the contents of the glass components SiO 2 , B 2 O 3 , Al 2 O 3 , Li 2 O, Na 2 O, K 2 O, Cs 2 O, MgO, CaO, SrO, BaO, ZnO, La 2 O 3 , Gd 2 O 3 , Y 2 O 3 , ZrO 2 , TiO 2 , Nb 2 O 5 , WO 3 and Bi 2 O 3 expressed in mass % are respectively C(SiO 2 ), C(B 2 O 3 ), C(Al 2 O 3 ), C(Li 2 O ), C(Na 2 O), C(K 2 O), C(Cs 2 O), C(MgO), C( CaO ), C(SrO), C(BaO), C(ZnO), C(La 2 O 3 ), C(Gd 2 O 3 ), and C(Cs 2 O ). O 3 ), C(Y 2 O 3 ), C(ZrO 2 ), C(TiO 2 ), C(Nb 2 O 5 ), C(WO 3 ) and C(Bi 2 O 3 ).
上述以外的玻璃成分Ta 2O 5、Sc 2O 3、HfO 2、Lu 2O 3、GeO 2及Yb 2O 3的以質量%表示的含量分別設為C(Ta 2O 5)、C(Sc 2O 3)、C(HfO 2)、C(Lu 2O 3)、C(GeO 2)及C(Yb 2O 3)。 The contents of the glass components Ta2O5 , Sc2O3 , HfO2 , Lu2O3 , GeO2 and Yb2O3 other than the above are expressed in mass % as C( Ta2O5 ) , C( Sc2O3 ) , C( HfO2 ), C( Lu2O3 ), C( GeO2 ) and C( Yb2O3 ) , respectively .
在第3實施方式中，將SiO 2、BO 1.5、AlO 1.5、LiO 0.5、NaO 0.5、KO 0.5、CsO 0.5、MgO、CaO、SrO、BaO、ZnO、LaO 1.5、GdO 1.5、YO 1.5、ZrO 2、TiO 2、NbO 2.5、WO 3及BiO 1.5的各化學式量分別設為M(SiO 2)、M(BO 1.5)、M(AlO 1.5)、M(LiO 0.5)、M(NaO 0.5)、M(KO 0.5)、M(CsO 0.5)、M(MgO)、M(CaO)、M(SrO)、M(BaO)、M(ZnO)、M(LaO 1.5)、M(GdO 1.5)、M(YO 1.5)、M(ZrO 2)、M(TiO 2)、M(NbO 2.5)、M(WO 3)及M(BiO 1.5)。 In the third embodiment, the chemical formulae of SiO 2 , BO 1.5 , AlO 1.5 , LiO 0.5 , NaO 0.5 , KO 0.5 , CsO 0.5 , MgO, CaO, SrO, BaO, ZnO, LaO 1.5 , GdO 1.5 , YO 1.5 , ZrO 2 , TiO 2 , NbO 2.5 , WO 3 and BiO 1.5 are M(SiO 2 ), M(BO 1.5 ), M(AlO 1.5 ) , M(LiO 0.5 ), M(NaO 0.5 ), M(KO 0.5 ), M(CsO 0.5 ) , M(MgO), M(CaO), M(SrO), M(BaO), M(ZnO), M(LaO 3) and BiO 1.5, respectively. 1.5 ), M(GdO 1.5 ), M(YO 1.5 ), M(ZrO 2 ), M(TiO 2 ), M(NbO 2.5 ), M(WO 3 ) and M(BiO 1.5 ).
上述以外的玻璃成分TaO 2.5、ScO 1.5、HfO 2、LuO 1.5、GeO 2及YbO 1.5的各化學式量分別設為M(TaO 2.5)、M(ScO 1.5)、M(HfO 2)、M(LuO 1.5)、M(GeO 2)及M(YbO 1.5)。 The chemical formulae of the glass components TaO 2.5 , ScO 1.5 , HfO 2 , LuO 1.5 , GeO 2 , and YbO 1.5 other than the above are M(TaO 2.5 ), M(ScO 1.5 ), M(HfO 2 ), M(LuO 1.5 ), M(GeO 2 ), and M(YbO 1.5 ), respectively.
即，在第3實施方式中，例如關於氧化物X yO z，可以將以質量%表示的含量設為C(X yO z)。另外，可以將氧化物X yO z中的平均每1莫耳陽離子(陽離子「X」)的化學式量、即XO z/y中的化學式量設為M(XO z/y)。而且，以{C(X yO z)/M(XO z/y)}表示的是以莫耳%表示的陽離子「X」的含量、即以陽離子%表示的「X」的含量。 That is, in the third embodiment, for example, regarding the oxide XyOz , the content expressed in mass% can be set to C( XyOz ). In addition, the chemical formula weight per 1 mol of cations (cation "X " ) in the oxide XyOz , that is, the chemical formula weight in XOz /y can be set to M(XOz /y ). Moreover, what is expressed by {C( XyOz )/M( XOz/y )} is the content of cations "X" expressed in mole%, that is, the content of "X" expressed in cation %.
在第3實施方式的光學玻璃中，設定A1＝{C(B 2O 3)/M(BO 1.5)}/{C(B 2O 3)/M(BO 1.5)+C(SiO 2)/M(SiO 2)}時，A1為1/3以上。A1的下限較佳為1.1/3，進一步以1.2/3、1.3/3、1.4/3、1.5/3、1.6/3、1.7/3、1.8/3、1.9/3的順序更佳。另外，A1的上限較佳為3.0/3，進一步以2.9/3、2.8/3、2.7/3、2.6/3、2.5/3、2.4/3、2.3/3的順序更佳。 In the optical glass of the third embodiment, when A1={C(B 2 O 3 )/M(BO 1.5 )}/{C(B 2 O 3 )/M(BO 1.5 )+C(SiO 2 )/M(SiO 2 )}, A1 is 1/3 or more. The lower limit of A1 is preferably 1.1/3, and more preferably in the order of 1.2/3, 1.3/3, 1.4/3, 1.5/3, 1.6/3, 1.7/3, 1.8/3, and 1.9/3. The upper limit of A1 is preferably 3.0/3, and more preferably in the order of 2.9/3, 2.8/3, 2.7/3, 2.6/3, 2.5/3, 2.4/3, and 2.3/3.
藉由將A1設為上述範圍，能夠得到在-30~70℃下的平均線膨脹係數α L大的低色散的光學玻璃。另外，能夠降低玻璃的相對折射率的溫度係數(dn/dT)。此外，即使在大量含有La 2O 3的情況下，也能夠抑制玻璃的熱穩定性的降低。另一方面，A1過小時，在大量包含作為提高折射率nd、防止平均線膨脹係數α L的降低的玻璃成分的La 2O 3及Y 2O 3的情況下，存在玻璃變得不穩定之虞。另外，A1過大時，存在玻璃的穩定性、化學耐久性及機械特性降低之虞。 By setting A1 to the above range, a low-dispersion optical glass having a large average linear expansion coefficient α L at -30 to 70°C can be obtained. In addition, the temperature coefficient of the relative refractive index of the glass (dn/dT) can be reduced. In addition, even when a large amount of La 2 O 3 is contained, a decrease in the thermal stability of the glass can be suppressed. On the other hand, when A1 is too small, when a large amount of La 2 O 3 and Y 2 O 3 are contained as glass components for increasing the refractive index nd and preventing a decrease in the average linear expansion coefficient α L, there is a risk that the glass will become unstable. In addition, when A1 is too large, there is a risk that the stability, chemical durability and mechanical properties of the glass will be reduced.
在第3實施方式的光學玻璃中，設定B1＝{C(BaO)/M(BaO)+C(SrO)/M(SrO)}/{C(Li 2O)/M(LiO 0.5)+C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(Cs 2O)/M(CsO 0.5)+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}時，B1為0.62以上。B1的下限較佳為0.63，進一步以0.65、0.67、0.69、0.71、0.73、0.75、0.77、0.79、0.81、0.83、0.85、0.87的順序更佳。另外，B1的上限較佳為1.00，進一步以0.99、0.98的順序更佳。B1也可以為1.00。 In the optical glass of the third embodiment, when B1={C(BaO)/M(BaO)+C(SrO)/M(SrO)}/{C( Li2O )/M( LiO0.5 )+C( Na2O )/M( NaO0.5 )+C( K2O )/M( KO0.5 )+C( Cs2O )/M( CsO0.5 )+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}, B1 is 0.62 or more. The lower limit of B1 is preferably 0.63, and more preferably in the order of 0.65, 0.67, 0.69, 0.71, 0.73, 0.75, 0.77, 0.79, 0.81, 0.83, 0.85, and 0.87. In addition, the upper limit of B1 is preferably 1.00, and more preferably in the order of 0.99 and 0.98. B1 may also be 1.00.
藉由將B1設為上述範圍，可得到平均線膨脹係數α L大的高折射率的光學玻璃。另外，能夠增大平均線膨脹係數α L，並且抑制熱穩定性的降低。另一方面，B1過小時，存在平均線膨脹係數α L及折射率nd降低、玻璃的穩定性受損之虞。 By setting B1 to the above range, an optical glass having a large average linear expansion coefficient α L and a high refractive index can be obtained. In addition, the average linear expansion coefficient α L can be increased and the decrease in thermal stability can be suppressed. On the other hand, when B1 is too small, there is a possibility that the average linear expansion coefficient α L and the refractive index nd decrease, and the stability of the glass may be impaired.
在第3實施方式的光學玻璃中，設定C1＝{C(BaO)/M(BaO)+C(Li 2O)/M(LiO 0.5)}/{C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(SiO 2)/M(SiO 2)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)}時，C1為8/9以上。C1的下限較佳為8.2/9，進一步以8.4/9、8.6/9、8.8/9、9.0/9、9.2/9、9.4/9、9.5/9的順序更佳。另外，C1的上限較佳為27/9，進一步以25/9、23/9、21/9、19/9、17/9、15/9、13/9、12/9的順序更佳。 In the optical glass of the third embodiment, when C1={C(BaO)/M(BaO)+C(Li 2 O)/M(LiO 0.5 )}/{C(Na 2 O)/M(NaO 0.5 )+C(K 2 O)/M(KO 0.5 )+C(SiO 2 )/M(SiO 2 )+C(TiO 2 )/M(TiO 2 )+C(Nb 2 O 5 )/M(NbO 2.5 )+C(WO 3 )/M(WO 3 )}, C1 is 8/9 or more. The lower limit of C1 is preferably 8.2/9, more preferably in the order of 8.4/9, 8.6/9, 8.8/9, 9.0/9, 9.2/9, 9.4/9, and 9.5/9. In addition, the upper limit of C1 is preferably 27/9, and further preferably in the order of 25/9, 23/9, 21/9, 19/9, 17/9, 15/9, 13/9, and 12/9.
藉由將C1設為上述範圍，可得到平均線膨脹係數α L大的高折射率低色散性的光學玻璃。另外，能夠降低玻璃的相對折射率的溫度係數(dn/dT)。另一方面，C1過小時，存在平均線膨脹係數α L降低、玻璃的高折射低色散性損失之虞。另外，C1過大時，存在玻璃的穩定性降低之虞。 By setting C1 to the above range, an optical glass with a high refractive index and low dispersion having a large average linear expansion coefficient α L can be obtained. In addition, the temperature coefficient (dn/dT) of the relative refractive index of the glass can be reduced. On the other hand, when C1 is too small, there is a risk that the average linear expansion coefficient α L is reduced and the high refractive index and low dispersion of the glass are lost. In addition, when C1 is too large, there is a risk that the stability of the glass is reduced.
在第3實施方式的光學玻璃中，設定D1＝C(Gd 2O 3)+C(ZnO)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)+C(ZrO 2)時，D1為13.50以下。D1的上限較佳為12.00，進一步以11.00、10.50、10.00、9.50、9.00、8.50的順序更佳。另外，D1的下限較佳為0，進一步以1、2、3、4、5、6、7、8的順序更佳。D1也可以為0。 In the optical glass of the third embodiment, when D1=C( Gd2O3 ) +C(ZnO)+C( TiO2 )+C( Nb2O5 )+C( WO3 )+C( ZrO2 ), D1 is 13.50 or less. The upper limit of D1 is preferably 12.00, more preferably in the order of 11.00, 10.50, 10.00, 9.50, 9.00, and 8.50. The lower limit of D1 is preferably 0, more preferably in the order of 1, 2 , 3, 4, 5, 6, 7, and 8. D1 may be 0.
藉由將D1設為上述範圍，能夠抑制平均線膨脹係數α L的降低。另外，可抑制高色散化，得到高折射率低色散性的光學玻璃。此外，還具有不增大玻璃的相對折射率的溫度係數(dn/dT)的效果。D1可以為0，但為了調整阿貝數νd等光學常數，也可以將D1設為大於0。另一方面，D1過大時，存在平均線膨脹係數α L降低、並且玻璃的高折射低色散性喪失之虞。 By setting D1 to the above range, the decrease in the average linear expansion coefficient α L can be suppressed. In addition, high dispersion can be suppressed to obtain an optical glass with a high refractive index and low dispersion. In addition, it also has the effect of not increasing the temperature coefficient (dn/dT) of the relative refractive index of the glass. D1 can be 0, but in order to adjust optical constants such as the Abbe number νd, D1 can also be set to be greater than 0. On the other hand, when D1 is too large, there is a risk that the average linear expansion coefficient α L is reduced and the high refractive index and low dispersion of the glass are lost.
在第3實施方式的光學玻璃中，設定E1＝{C(La 2O 3)+C(Gd 2O 3)+C(Y 2O 3)}/{C(SiO 2)+C(B 2O 3)+C(Al 2O 3)}時，E1為1.25以上。E1的下限較佳為1.30，進一步以1.35、1.40、1.45、1.50、1.55、1.60、1.65、1.70的順序更佳。另外，E1的上限較佳為3.00，進一步以2.80、2.60、2.40、2.20、2.10的順序更佳。 In the optical glass of the third embodiment, when E1={C(La 2 O 3 )+C(Gd 2 O 3 )+C(Y 2 O 3 )}/{C(SiO 2 )+C(B 2 O 3 )+C(Al 2 O 3 )}, E1 is 1.25 or more. The lower limit of E1 is preferably 1.30, more preferably in the order of 1.35, 1.40, 1.45, 1.50, 1.55, 1.60, 1.65, and 1.70. The upper limit of E1 is preferably 3.00, more preferably in the order of 2.80, 2.60, 2.40, 2.20, and 2.10.
藉由將E1設為上述範圍，可得到高折射率低色散性的光學玻璃。另一方面，E1過小時，存在玻璃的高折射高色散性損失、平均線膨脹係數α L降低之虞。另外，E1過大時，存在玻璃的熱穩定性降低之虞。 By setting E1 to the above range, an optical glass with high refractive index and low dispersion can be obtained. On the other hand, when E1 is too small, there is a risk that the high refractive index and high dispersion of the glass will be lost and the average linear expansion coefficient α L will decrease. In addition, when E1 is too large, there is a risk that the thermal stability of the glass will decrease.
在第3實施方式的光學玻璃中，設定F1＝{C(Gd 2O 3)/M(GdO 1.5)+C(ZnO)/M(ZnO)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)+C(Bi 2O 3)/M(BiO 1.5)}/{C(Y 2O 3)/M(YO 1.5)}時，F1為2.0以下。F1的上限較佳為1.8，進一步以1.6、1.4、1.2、1.1、1.0、0.9、0.8、0.6的順序更佳。另外，F1的下限較佳為0，進一步以0.1、0.2、0.3、0.4的順序更佳。F1可以為0。 In the optical glass of the third embodiment, when F1={C( Gd2O3 )/M( GdO1.5 )+C ( ZnO )/M(ZnO)+C( TiO2 )/M(TiO2)+C( Nb2O5 )/M( NbO2.5 )+C( WO3 )/M( WO3 )+C(Bi2O3)/M( BiO1.5 )}/{C( Y2O3 )/M( YO1.5 )}, F1 is 2.0 or less. The upper limit of F1 is preferably 1.8, and more preferably in the order of 1.6 , 1.4, 1.2, 1.1, 1.0, 0.9 , 0.8 , and 0.6 . In addition, the lower limit of F1 is preferably 0, and more preferably in the order of 0.1, 0.2, 0.3, and 0.4. F1 can be 0.
藉由將F1設為上述範圍，可得到平均線膨脹係數α L大的光學玻璃。另外，能夠抑制玻璃的熱穩定性的降低。F1可以為0，但為了調整阿貝數νd等光學常數，也可以將F1設為大於0。另一方面，F1過大時，存在平均線膨脹係數α L降低、或失去玻璃的高折射低色散性之虞。 By setting F1 to the above range, an optical glass with a large average linear expansion coefficient α L can be obtained. In addition, the reduction in the thermal stability of the glass can be suppressed. F1 can be 0, but in order to adjust optical constants such as the Abbe number νd, F1 can also be set to be greater than 0. On the other hand, when F1 is too large, there is a risk that the average linear expansion coefficient α L will decrease or the high refractive and low dispersion properties of the glass will be lost.
在第3實施方式的光學玻璃中，設定G1＝C(BaO)/M(BaO)+C(La 2O 3)/M(LaO 1.5)+C(Li 2O)/M(LiO 0.5)+C(Y 2O 3)/M(YO 1.5)時，G1的下限較佳為0.47，進一步以0.475、0.48、0.485的順序更佳。另外，G1的上限較佳為0.60，進一步以0.59、0.58、0.57、0.56、0.55、0.54、0.53的順序更佳。 In the optical glass of the third embodiment, when G1=C(BaO)/M(BaO)+C(La 2 O 3 )/M(LaO 1.5 )+C(Li 2 O)/M(LiO 0.5 )+C(Y 2 O 3 )/M(YO 1.5 ), the lower limit of G1 is preferably 0.47, more preferably in the order of 0.475, 0.48, and 0.485. The upper limit of G1 is preferably 0.60, more preferably in the order of 0.59, 0.58, 0.57, 0.56, 0.55, 0.54, and 0.53.
從抑制平均線膨脹係數α L的降低、並且得到高折射率低色散性的光學玻璃的觀點考慮，較佳將G1設為上述範圍。另一方面，G1過小時，存在平均線膨脹係數α L降低、玻璃的高折射低色散性損失之虞。另外，G1過大時，存在玻璃的熱穩定性降低之虞。 From the viewpoint of suppressing the decrease of the average linear expansion coefficient α L and obtaining an optical glass with high refractive index and low dispersion, it is preferable to set G1 to the above range. On the other hand, when G1 is too small, there is a risk that the average linear expansion coefficient α L decreases and the high refractive index and low dispersion of the glass are lost. In addition, when G1 is too large, there is a risk that the thermal stability of the glass is reduced.
關於第3實施方式的光學玻璃中的上述以外的玻璃成分的含量及比率，以下示出非限定性實例。Regarding the contents and ratios of the glass components other than those described above in the optical glass according to the third embodiment, non-limiting examples are shown below.
在第3實施方式中，{C(B 2O 3)/M(BO 1.5)+C(SiO 2)/M(SiO 2)}的下限較佳為0.35，進一步以0.37、0.39、0.41、0.43、0.45、0.47的順序更佳。另外，其上限較佳為0.75，進一步以0.73、0.71、0.69、0.67、0.65、0.63、0.61、0.59的順序更佳。 In the third embodiment, the lower limit of {C( B2O3 )/M( BO1.5 )+C( SiO2 )/M( SiO2 )} is preferably 0.35, more preferably in the order of 0.37 , 0.39, 0.41, 0.43, 0.45, 0.47, and the upper limit is preferably 0.75, more preferably in the order of 0.73, 0.71, 0.69, 0.67, 0.65, 0.63, 0.61, 0.59.
從得到平均線膨脹係數α L大、低色散的光學玻璃的觀點考慮，{C(B 2O 3)/M(BO 1.5)+C(SiO 2)/M(SiO 2)}較佳設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L and low dispersion, {C(B 2 O 3 )/M(BO 1.5 )+C(SiO 2 )/M(SiO 2 )} is preferably set to be within the above range.
在第3實施方式中，{C(BaO)/M(BaO)+C(SrO)/M(SrO)}的下限較佳為0.15，進一步以0.16、0.17、0.18、0.19、0.20的順序更佳。另外，其上限較佳為0.30，進一步以0.29、0.28、0.27、0.26、0.25、0.24、0.23的順序更佳。In the third embodiment, the lower limit of {C(BaO)/M(BaO)+C(SrO)/M(SrO)} is preferably 0.15, and more preferably in the order of 0.16, 0.17, 0.18, 0.19, and 0.20. In addition, the upper limit is preferably 0.30, and more preferably in the order of 0.29, 0.28, 0.27, 0.26, 0.25, 0.24, and 0.23.
從得到平均線膨脹係數α L大、高折射率的光學玻璃的觀點考慮，{C(BaO)/M(BaO)+C(SrO)/M(SrO)}較佳設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L and a high refractive index, {C(BaO)/M(BaO)+C(SrO)/M(SrO)} is preferably set to the above range.
在第3實施方式中，{C(Li 2O)/M(LiO 0.5)+C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(Cs 2O)/M(CsO 0.5)+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}的下限較佳為0.15，進一步以0.16、0.17、0.18、0.19、0.20的順序更佳。另外，其上限較佳為0.35，進一步以0.34、0.33、0.32、0.31、0.30、0.29、0.28、0.27、0.26、0.25、0.24、0.23的順序更佳。 In the third embodiment, the lower limit of {C( Li2O )/M( LiO0.5 )+C( Na2O )/M( NaO0.5 )+C( K2O )/M( KO0.5 )+C( Cs2O)/M(CsO0.5 ) +C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)} is preferably 0.15, more preferably in the order of 0.16, 0.17, 0.18, 0.19, and 0.20. In addition, the upper limit is preferably 0.35, and more preferably in the order of 0.34, 0.33, 0.32, 0.31, 0.30, 0.29, 0.28, 0.27, 0.26, 0.25, 0.24, and 0.23.
從得到平均線膨脹系數α L大、高折射率的光學玻璃的觀點考慮，{C(Li 2O)/M(LiO 0.5)+C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(Cs 2O)/M(CsO 0.5)+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}較佳設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient αL and a high refractive index, {C( Li2O )/M( LiO0.5 )+C( Na2O )/M( NaO0.5 )+C(K2O)/M ( KO0.5 )+C(Cs2O)/M( CsO0.5 )+C( MgO )/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)} is preferably set to be in the above range.
在第3實施方式中，{C(BaO)/M(BaO)+C(Li 2O)/M(LiO 0.5)}的下限較佳為0.15，進一步以0.16、0.17、0.18、0.19、0.20的順序更佳。另外，其上限較佳為0.35，進一步以0.34、0.33、0.32、0.31、0.30、0.29、0.28、0.27、0.26、0.25、0.24、0.23的順序更佳。 In the third embodiment, the lower limit of {C(BaO)/M(BaO)+C( Li2O )/M( LiO0.5 )} is preferably 0.15, more preferably in the order of 0.16, 0.17, 0.18, 0.19, 0.20, and the upper limit is preferably 0.35, more preferably in the order of 0.34, 0.33, 0.32, 0.31, 0.30, 0.29, 0.28, 0.27, 0.26, 0.25, 0.24, 0.23.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點考慮，{C(BaO)/M(BaO)+C(Li 2O)/M(LiO 0.5)}較佳設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L and high refractive index and low dispersion, {C(BaO)/M(BaO)+C(Li 2 O)/M(LiO 0.5 )} is preferably set to be within the above range.
在第3實施方式中，{C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(SiO 2)/M(SiO 2)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)}的下限較佳為0.05，進一步以0.06、0.07、0.08、0.09、0.10、0.11、0.12、0.13、0.14、0.15、0.16的順序更佳。另外，其上限較佳為0.30，進一步以0.29、0.28、0.27、0.26、0.25、0.24、0.23、0.22、0.21的順序更佳。 In the third embodiment, the lower limit of {C( Na2O )/M( NaO0.5 )+C( K2O )/M( KO0.5 )+C( SiO2 )/M( SiO2 )+C(TiO2)/M( TiO2 )+C( Nb2O5 )/M( NbO2.5 )+C( WO3 )/M( WO3 )} is preferably 0.05, and more preferably in the order of 0.06, 0.07, 0.08, 0.09, 0.10, 0.11, 0.12, 0.13, 0.14, 0.15, and 0.16. In addition, the upper limit is preferably 0.30, and more preferably in the order of 0.29, 0.28, 0.27, 0.26, 0.25, 0.24, 0.23, 0.22, and 0.21.
從得到平均線膨脹系數α L大、高折射率低色散性的光學玻璃的觀點考慮，C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(SiO 2)/M(SiO 2)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)}較佳設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient αL , a high refractive index and low dispersion, C( Na2O )/M( NaO0.5 )+C( K2O )/M( KO0.5 )+C ( SiO2 )/M( SiO2 )+C( TiO2 )/M( TiO2 )+C( Nb2O5)/M(NbO2.5 ) +C( WO3 )/M( WO3 )} is preferably set to be in the above range.
在第3實施方式的光學玻璃中，質量比[C(BaO)/{C(SiO 2)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)}]的下限較佳為1.0，進一步以1.2、1.4、1.6、1.8、2.0、2.2、2.4的順序更佳。另外，該質量比的上限較佳為5.5，進一步以5.3、5.1、4.9、4.7、4.5、4.3、4.1、3.9、3.7、3.5的順序更佳。 In the optical glass of the third embodiment, the lower limit of the mass ratio [C(BaO)/{C( SiO2 )+C( TiO2 )+C( Nb2O5 )+C( WO3 )}] is preferably 1.0, more preferably in the order of 1.2, 1.4 , 1.6, 1.8, 2.0, 2.2, and 2.4. The upper limit of the mass ratio is preferably 5.5, more preferably in the order of 5.3, 5.1, 4.9, 4.7, 4.5, 4.3, 4.1, 3.9, 3.7, and 3.5.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點及減小相對折射率的溫度係數(dn/dT)的觀點考慮，較佳將質量比[C(BaO)/{C(SiO 2)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)}]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient αL , a high refractive index and low dispersion and from the viewpoint of reducing the temperature coefficient of relative refractive index (dn/dT), the mass ratio [C(BaO)/{C( SiO2 )+C( TiO2 )+C( Nb2O5 )+C( WO3 )}] is preferably set to the above range.
在第3實施方式的光學玻璃中，質量比[C(BaO)/{C(SiO 2)+C(B 2O 3)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)}]的下限較佳為0.80，進一步以0.85、0.90、0.95、1.00、1.05、1.10、1.15、1.20的順序更佳。另外，該質量比的上限較佳為1.70，進一步以1.65、1.60、1.55、1.50、1.45、1.40、1.35的順序更佳。 In the optical glass of the third embodiment, the lower limit of the mass ratio [C(BaO)/{C( SiO2 )+C( B2O3 ) +C( TiO2 )+C( Nb2O5 )+C( WO3 )}] is preferably 0.80, more preferably in the order of 0.85, 0.90, 0.95, 1.00, 1.05, 1.10 , 1.15, and 1.20. The upper limit of the mass ratio is preferably 1.70, more preferably in the order of 1.65, 1.60, 1.55, 1.50, 1.45, 1.40, and 1.35.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點及減小相對折射率的溫度係數(dn/dT)的溫度依賴性的觀點考慮，較佳將質量比[C(BaO)/{C(SiO 2)+C(B 2O 3)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)}]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient αL , a high refractive index and low dispersion and from the viewpoint of reducing the temperature dependence of the temperature coefficient of relative refractive index (dn/dT), it is preferred to set the mass ratio [C(BaO)/{C(SiO 2 )+C(B 2 O 3 )+C(TiO 2 )+C(Nb 2 O 5 )+C(WO 3 )}] to the above range.
在第3實施方式的光學玻璃中，質量比[{C(BaO)+C(Li 2O)+C(SrO)}/{C(SiO 2)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)}]的下限較佳為0.5，進一步以1.0、1.5、2.0、2.2、2.4的順序更佳。另外，該質量比的上限較佳為7.0，進一步以6.5、6.0、5.5、5.0、4.5、4.0、3.5的順序更佳。 In the optical glass of the third embodiment, the lower limit of the mass ratio [{C(BaO)+C( Li2O )+C(SrO)}/{C( SiO2 )+C( TiO2 )+C( Nb2O5 ) +C( WO3 )}] is preferably 0.5, more preferably in the order of 1.0, 1.5, 2.0, 2.2, and 2.4. The upper limit of the mass ratio is preferably 7.0, more preferably in the order of 6.5, 6.0, 5.5, 5.0, 4.5, 4.0, and 3.5.
從得到平均線膨脹係數α L大、高折射率低色散性的光學玻璃的觀點考慮，較佳將質量比[{C(BaO)+C(Li 2O)+C(SrO)}/{C(SiO 2)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)}]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient αL , a high refractive index and low dispersion, it is preferred that the mass ratio [{C(BaO)+C( Li2O )+C(SrO)}/{C( SiO2 )+C( TiO2 )+C (Nb2O5 ) +C( WO3 )}] be within the above range.
在第3實施方式的光學玻璃中，質量比[{C(Li 2O)+C(Na 2O)+C(K 2O)+C(Cs 2O)+C(CaO)+C(SrO)+C(BaO)}/{C(SiO 2)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)}]的下限較佳為0.5，進一步以1.0、1.5、2.0、2.2、2.4的順序更佳。另外，該質量比的上限較佳為7.0，進一步以6.5、6.0、5.5、5.0、4.5、4.0、3.5的順序更佳。 In the optical glass of the third embodiment, the lower limit of the mass ratio [{C( Li2O )+C( Na2O )+C( K2O )+C( Cs2O )+C(CaO)+C(SrO)+C(BaO)}/{C( SiO2 )+C( TiO2 )+C( Nb2O5 )+C( WO3 )}] is preferably 0.5, more preferably in the order of 1.0, 1.5, 2.0 , 2.2, and 2.4. The upper limit of the mass ratio is preferably 7.0, more preferably in the order of 6.5, 6.0, 5.5, 5.0, 4.5, 4.0, and 3.5.
從得到平均線膨脹系數α L大、高折射率低色散性的光學玻璃的觀點考慮，較佳將質量比[{C(Li 2O)+C(Na 2O)+C(K 2O)+C(Cs 2O)+C(CaO)+C(SrO)+C(BaO)}/{C(SiO 2)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)}]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient αL , a high refractive index and low dispersion, it is preferable to set the mass ratio [{C( Li2O )+C( Na2O )+C( K2O )+C( Cs2O )+C(CaO)+C(SrO)+C(BaO)}/{C( SiO2 )+C( TiO2 )+C( Nb2O5 )+C( WO3 )}] to the above range.
在第3實施方式的光學玻璃中，合計含量[C(ZnO)+C(Gd 2O 3)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)]的下限較佳為0，進一步以1、2、3、4、5的順序更佳。該合計含量可以為0。另外，該合計含量的上限較佳為15，進一步以14、13、12、11、10、9、8、7、6的順序更佳。 In the optical glass of the third embodiment, the lower limit of the total content [C(ZnO)+C( Gd2O3 )+C( TiO2 )+C( Nb2O5 )+C( WO3 )] is preferably 0, more preferably in the order of 1 , 2, 3 , 4, and 5. The total content may be 0. In addition, the upper limit of the total content is preferably 15, more preferably in the order of 14, 13, 12, 11, 10, 9, 8, 7, and 6.
從得到平均線膨脹係數α L大、色散小的光學玻璃的觀點考慮，較佳將合計含量[C(ZnO)+C(Gd 2O 3)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient α L and small dispersion, the total content [C(ZnO)+C(Gd 2 O 3 )+C(TiO 2 )+C(Nb 2 O 5 )+C(WO 3 )] is preferably set to the above range.
在第3實施方式的光學玻璃中，合計含量[C(SiO 2)+C(ZnO)+C(Gd 2O 3)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)]的下限較佳為5，進一步以6、7、8、9的順序更佳。另外，該合計含量的上限較佳為25，進一步以24、23、22、21、20、19、18、17、16、15、14的順序更佳。 In the optical glass of the third embodiment, the lower limit of the total content [C( SiO2 )+C(ZnO)+C ( Gd2O3 )+C( TiO2 )+C( Nb2O5 )+C( WO3 )] is preferably 5 , more preferably in the order of 6, 7, 8, and 9. The upper limit of the total content is preferably 25, more preferably in the order of 24, 23, 22, 21, 20, 19, 18, 17, 16, 15, and 14.
從得到平均線膨脹係數α L大、且高折射率低色散性的光學玻璃的觀點考慮，較佳將合計含量[C(SiO 2)+C(ZnO)+C(Gd 2O 3)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient αL , a high refractive index and low dispersion, the total content [C( SiO2 )+C(ZnO)+C( Gd2O3 )+C( TiO2 ) +C( Nb2O5 ) +C( WO3 )] is preferably within the above range.
在第3實施方式的光學玻璃中，合計含量[C(SiO 2)+C(ZnO)+C(Gd 2O 3)+C(ZrO 2)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)]的下限較佳為5，進一步以6、7、8、9的順序更佳。另外，該合計含量的上限較佳為25，進一步以24、23、22、21、20、19、18、17、16的順序更佳。 In the optical glass of the third embodiment, the lower limit of the total content [C( SiO2 )+C(ZnO)+C( Gd2O3 )+C( ZrO2 )+C( TiO2 )+C( Nb2O5 )+ C ( WO3 )] is preferably 5, more preferably in the order of 6, 7, 8, and 9. The upper limit of the total content is preferably 25, more preferably in the order of 24, 23, 22, 21, 20, 19, 18 , 17, and 16.
從得到平均線膨脹係數α L大、且高折射率低色散性的光學玻璃的觀點考慮，較佳將合計含量[C(SiO 2)+C(ZnO)+C(Gd 2O 3)+C(ZrO 2)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient αL , a high refractive index and low dispersion, the total content [C( SiO2 )+C(ZnO)+C( Gd2O3 ) +C( ZrO2 )+C( TiO2 )+C ( Nb2O5 )+C( WO3 )] is preferably within the above range.
在第3實施方式的光學玻璃中，合計含量[C(Al 2O 3)+C(SiO 2)+C(ZnO)+C(Gd 2O 3)+C(ZrO 2)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)]的下限較佳為5，進一步以6、7、8、9的順序更佳。另外，該合計含量的上限較佳為25，進一步以24、23、22、21、20、19、18、17、16的順序更佳。 In the optical glass of the third embodiment, the lower limit of the total content [C( Al2O3 ) + C ( SiO2 )+C(ZnO)+C( Gd2O3 )+C( ZrO2 )+C(TiO2)+C( Nb2O5 )+C( WO3 )] is preferably 5, more preferably in the order of 6 , 7 , 8 , and 9. The upper limit of the total content is preferably 25, more preferably in the order of 24, 23, 22, 21, 20, 19, 18, 17, and 16.
從得到平均線膨脹係數α L大、且高折射率低色散性的光學玻璃的觀點考慮，較佳將合計含量[C(Al 2O 3)+C(SiO 2)+C(ZnO)+C(Gd 2O 3)+C(ZrO 2)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)]設為上述範圍。 From the viewpoint of obtaining an optical glass having a large average linear expansion coefficient αL , a high refractive index and low dispersion, the total content [C( Al2O3 )+C( SiO2 )+C(ZnO)+C ( Gd2O3 )+C( ZrO2 )+ C ( TiO2 )+C( Nb2O5 )+C( WO3 )] is preferably within the above range.
在第3實施方式中，合計含量[C(La 2O 3)+C(Gd 2O 3)+C(Y 2O 3)]的下限較佳為25，進一步以26、27、28、29、30、31、32、33、34、35、36、37、38的順序更佳。另外，該合計含量的上限較佳為50，進一步以49、48、47、46、45、44、43的順序更佳。 In the third embodiment, the lower limit of the total content [C( La2O3 ) +C( Gd2O3 ) +C( Y2O3 ) ] is preferably 25, more preferably in the order of 26, 27, 28, 29, 30, 31, 32, 33, 34, 35, 36, 37, 38. The upper limit of the total content is preferably 50, more preferably in the order of 49, 48, 47, 46, 45, 44, 43.
從得到高折射率低色散性的光學玻璃的觀點考慮，合計含量[C(La 2O 3)+C(Gd 2O 3)+C(Y 2O 3)]較佳設為上述範圍。 From the viewpoint of obtaining an optical glass with a high refractive index and low dispersion, the total content [C(La 2 O 3 )+C(Gd 2 O 3 )+C(Y 2 O 3 )] is preferably within the above range.
在第3實施方式中，合計含量[C(SiO 2)+C(B 2O 3)+C(Al 2O 3)]的下限較佳為15，進一步以16、17、18、19的順序更佳。另外，該合計含量的上限較佳為30，進一步以29、28、27、26、25的順序更佳。 In the third embodiment, the lower limit of the total content [C( SiO2 )+C( B2O3 )+C( Al2O3 )] is preferably 15, more preferably in the order of 16, 17, 18 , and 19. The upper limit of the total content is preferably 30, more preferably in the order of 29, 28, 27, 26, and 25.
從盡可能不降低折射率、而得到高折射率低色散性的光學玻璃的觀點考慮，合計含量[C(SiO 2)+C(B 2O 3)+C(Al 2O 3)]較佳設為上述範圍。 From the viewpoint of obtaining an optical glass with a high refractive index and low dispersion without lowering the refractive index as much as possible, the total content [C(SiO 2 )+C(B 2 O 3 )+C(Al 2 O 3 )] is preferably within the above range.
在第3實施方式的光學玻璃中，質量比[{C(La 2O 3)+C(Gd 2O 3)+C(Y 2O 3)}/{2×C(SiO 2)+C(B 2O 3)+C(Al 2O 3)}]的下限較佳為1.00，進一步以1.05、1.10、1.15、1.16、1.17、1.18、1.19、1.20、1.21的順序更佳。另外，該質量比的上限較佳為1.80，進一步以1.75、1.70、1.65、1.60、1.55、1.54、1.53、1.52、1.51、1.50的順序更佳。 In the optical glass of the third embodiment, the lower limit of the mass ratio [{C( La2O3 ) +C( Gd2O3 )+C( Y2O3 ) }/{2×C( SiO2 )+C( B2O3 ) +C( Al2O3 )}] is preferably 1.00, more preferably in the order of 1.05, 1.10, 1.15, 1.16, 1.17 , 1.18, 1.19, 1.20 , and 1.21. The upper limit of the mass ratio is preferably 1.80, more preferably in the order of 1.75, 1.70, 1.65, 1.60, 1.55, 1.54, 1.53, 1.52, 1.51, and 1.50.
從得到高折射率低色散性的光學玻璃的觀點考慮，質量比[{C(La 2O 3)+C(Gd 2O 3)+C(Y 2O 3)}/{2×C(SiO 2)+C(B 2O 3)+C(Al 2O 3)}]較佳設為上述範圍。 From the viewpoint of obtaining an optical glass with a high refractive index and low dispersion, the mass ratio [{C( La2O3 ) + C ( Gd2O3 )+C( Y2O3 )}/{2xC ( SiO2 )+C( B2O3 ) +C( Al2O3 )}] is preferably within the above range.
在第3實施方式的光學玻璃中，合計含量[2×C(SiO 2)+C(B 2O 3)+C(Al 2O 3)]的下限較佳為20，進一步以21、22、23、24、25、26的順序更佳。另外，該合計含量的上限較佳為45，進一步以44、43、42、41、40、39、38、37、36、35的順序更佳。 In the optical glass of the third embodiment, the lower limit of the total content [2×C(SiO 2 )+C(B 2 O 3 )+C(Al 2 O 3 )] is preferably 20, more preferably in the order of 21, 22, 23, 24, 25, and 26. The upper limit of the total content is preferably 45, more preferably in the order of 44, 43, 42, 41, 40, 39, 38, 37, 36, and 35.
從得到平均線膨脹係數α L大的高折射率低色散性的光學玻璃的觀點考慮，合計含量[2×C(SiO 2)+C(B 2O 3)+C(Al 2O 3)]較佳設為上述範圍。 From the viewpoint of obtaining an optical glass having a high refractive index and low dispersion and having a large average linear expansion coefficient α L , the total content [2×C(SiO 2 )+C(B 2 O 3 )+C(Al 2 O 3 )] is preferably within the above range.
在第3實施方式的光學玻璃中，質量比[{C(La 2O 3)+C(Y 2O 3)}/{C(B 2O 3)+C(BaO)}]的下限較佳為0.50，進一步以0.55、0.60、0.65、0.70、0.75、0.80的順序更佳。另外，該質量比的上限較佳為1.30，進一步以1.25、1.20、1.15、1.10、1.05、1.00、0.95、0.92的順序更佳。 In the optical glass of the third embodiment, the lower limit of the mass ratio [{C( La2O3 ) +C( Y2O3 )}/{C( B2O3 ) +C(BaO)}] is preferably 0.50, more preferably in the order of 0.55, 0.60, 0.65, 0.70, 0.75 , and 0.80. The upper limit of the mass ratio is preferably 1.30, more preferably in the order of 1.25, 1.20, 1.15, 1.10, 1.05, 1.00, 0.95, and 0.92.
從得到高折射率低色散性的光學玻璃的觀點考慮，質量比[{C(La 2O 3)+C(Y 2O 3)}/{C(B 2O 3)+C(BaO)}]較佳設為上述範圍。 From the viewpoint of obtaining an optical glass with a high refractive index and low dispersion, the mass ratio [{C(La 2 O 3 )+C(Y 2 O 3 )}/{C(B 2 O 3 )+C(BaO)}] is preferably set to be within the above range.
在第3實施方式中，[C(Gd 2O 3)/M(GdO 1.5)+C(ZnO)/M(ZnO)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)+C(Bi 2O 3)/M(BiO 1.5)]的下限較佳為0，進一步以0.01、0.02、0.03、0.04、0.05、0.06的順序更佳。該值可以為0。另外，其上限較佳為0.30，進一步以0.25、0.20、0.18、0.16、0.14、0.12、0.10、0.08的順序更佳。 In the third embodiment, the lower limit of [C( Gd2O3 )/M( GdO1.5 )+C(ZnO)/M(ZnO)+C( TiO2 )/M( TiO2 )+C( Nb2O5)/M(NbO2.5 ) + C(WO3)/M( WO3 )+C( Bi2O3 )/M( BiO1.5 )] is preferably 0, more preferably in the order of 0.01, 0.02, 0.03, 0.04 , 0.05 , and 0.06. This value may be 0. In addition, the upper limit is preferably 0.30, and more preferably in the order of 0.25, 0.20, 0.18, 0.16, 0.14, 0.12, 0.10, and 0.08.
從平均線膨脹系數α L大、抑制玻璃的熱稳定性的降低的觀點考慮，[C(Gd 2O 3)/M(GdO 1.5)+C(ZnO)/M(ZnO)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)+C(Bi 2O 3)/M(BiO 1.5)]較佳設為上述範圍。 From the viewpoint of increasing the average linear expansion coefficient αL and suppressing a decrease in the thermal stability of the glass, [ C ( Gd2O3 )/M( GdO1.5 )+ C (ZnO)/M(ZnO)+C( TiO2 )/M( TiO2 )+C(Nb2O5)/M ( NbO2.5 )+C( WO3 )/M( WO3 )+C( Bi2O3 )/M( BiO1.5 )] is preferably within the above range.
在第3實施方式的光學玻璃中，質量比[C(Y 2O 3)/{C(La 2O 3)+C(Y 2O 3)+C(Gd 2O 3)}]的下限較佳為0.20，進一步以0.21、0.22、0.23、0.24、0.25、0.26、0.27、0.28、0.29、0.30、0.31、0.32、0.33、0.34的順序更佳。另外，該質量比的上限較佳為0.60，進一步以0.59、0.58、0.57、0.56、0.55、0.54、0.53、0.52、0.51、0.50、0.49、0.48、0.47、0.46的順序更佳。 In the optical glass of the third embodiment, the lower limit of the mass ratio [C( Y2O3 )/{C( La2O3 ) +C( Y2O3 ) +C( Gd2O3 ) }] is preferably 0.20, and more preferably in the order of 0.21, 0.22, 0.23, 0.24, 0.25, 0.26, 0.27, 0.28, 0.29, 0.30, 0.31, 0.32 , 0.33 , and 0.34. In addition, the upper limit of the mass ratio is preferably 0.60, and more preferably in the order of 0.59, 0.58, 0.57, 0.56, 0.55, 0.54, 0.53, 0.52, 0.51, 0.50, 0.49, 0.48, 0.47, and 0.46.
從平均線膨脹係數α L大、抑制玻璃的熱穩定性的降低的觀點考慮，較佳將質量比[C(Y 2O 3)/{C(La 2O 3)+C(Y 2O 3)+C(Gd 2O 3)}]設為上述範圍。 From the viewpoint of increasing the average linear expansion coefficient αL and suppressing a decrease in the thermal stability of the glass, it is preferred that the mass ratio [C( Y2O3 )/{C( La2O3 )+C( Y2O3 ) +C( Gd2O3 ) }] be within the above range.
在第3實施方式的光學玻璃中，質量比[C(Y 2O 3)/{C(La 2O 3)+C(Y 2O 3)+C(TiO 2)}]的下限較佳為0.20，進一步以0.21、0.22、0.23、0.24、0.25、0.26、0.27、0.28、0.29、0.30、0.31、0.32的順序更佳。另外，該質量比的上限較佳為0.50，進一步以0.49、0.48、0.47、0.46、0.45的順序更佳。 In the optical glass of the third embodiment, the lower limit of the mass ratio [C( Y2O3 )/{C( La2O3 )+C( Y2O3 ) +C( TiO2 )}] is preferably 0.20, more preferably in the order of 0.21, 0.22, 0.23, 0.24, 0.25, 0.26 , 0.27 , 0.28, 0.29, 0.30, 0.31, 0.32. The upper limit of the mass ratio is preferably 0.50, more preferably in the order of 0.49, 0.48, 0.47, 0.46, 0.45.
從平均線膨脹係數α L大、抑制玻璃的熱穩定性的降低的觀點考慮，較佳將質量比[C(Y 2O 3)/{C(La 2O 3)+C(Y 2O 3)+C(TiO 2)}]設為上述範圍。 From the viewpoint of increasing the average linear expansion coefficient αL and suppressing a decrease in the thermal stability of the glass, it is preferred that the mass ratio [C(Y 2 O 3 )/{C(La 2 O 3 )+C(Y 2 O 3 )+C(TiO 2 )}] be within the above range.
在第3實施方式的光學玻璃中，合計含量[C(BaO)+C(La 2O 3)+C(Y 2O 3)]的下限較佳為50，進一步以52、54、56、58、60、62、64、66、68、70的順序更佳。另外，該合計含量的上限較佳為85，進一步以83、81、79、77、76的順序更佳。 In the optical glass of the third embodiment, the lower limit of the total content [C(BaO)+C( La2O3 )+C( Y2O3 ) ] is preferably 50, more preferably in the order of 52, 54, 56, 58, 60, 62, 64, 66, 68 , 70. The upper limit of the total content is preferably 85, more preferably in the order of 83, 81, 79, 77, 76.
從抑制平均線膨脹係數α L的降低、並且得到高折射率低色散性的光學玻璃的觀點考慮，較佳將合計含量[C(BaO)+C(La 2O 3)+C(Y 2O 3)]設為上述範圍。 From the viewpoint of suppressing a decrease in the average linear expansion coefficient α L and obtaining an optical glass with a high refractive index and low dispersion, the total content [C(BaO)+C(La 2 O 3 )+C(Y 2 O 3 )] is preferably within the above range.
在第3實施方式的光學玻璃中，SiO 2的含量的下限較佳為3.0%，進一步以3.5%、4.0%、4.5%、5.0%、5.5%、6.0%、6.5%、7.0%的順序更佳。另外，SiO 2的含量的上限較佳為15.0%，進一步以14.5%、14.0%、13.5%、13.0%、12.5%、12.0%、11.5%、11.0%、10.5%、10.0%的順序更佳。 In the optical glass of the third embodiment, the lower limit of the content of SiO2 is preferably 3.0%, and more preferably in the order of 3.5%, 4.0%, 4.5%, 5.0%, 5.5%, 6.0%, 6.5%, and 7.0%. In addition, the upper limit of the content of SiO2 is preferably 15.0%, and more preferably in the order of 14.5%, 14.0%, 13.5%, 13.0%, 12.5%, 12.0%, 11.5%, 11.0%, 10.5%, and 10.0%.
SiO 2為玻璃的網絡形成成分，具有改善玻璃的熱穩定性、化學耐久性、耐候性、提高熔融玻璃的黏度、容易將熔融玻璃成型的作用。另一方面，SiO 2的含量多時，除了平均線膨脹係數α L比較容易降低以外，還存在折射率nd降低之虞。因此，SiO 2的含量較佳為上述範圍。 SiO2 is a network-forming component of glass, and has the effects of improving the thermal stability, chemical durability, and weather resistance of glass, increasing the viscosity of molten glass, and facilitating the molding of molten glass. On the other hand, when the content of SiO2 is high, in addition to the average linear expansion coefficient αL being relatively easy to decrease, there is also the risk of a decrease in the refractive index nd. Therefore, the content of SiO2 is preferably within the above range.
在第3實施方式的光學玻璃中，B 2O 3的含量的下限較佳為8.0%，進一步以8.5%、9.0%、9.5%、10.0%、10.5%、11.0%、11.5%、12.0%的順序更佳。另外，B 2O 3的含量的上限較佳為20.0%，進一步以19.5%、19.0%、18.5%、18.0%、17.5%、17.0%、16.5%、16.0%、15.5%、15.0%的順序更佳。 In the optical glass of the third embodiment, the lower limit of the content of B2O3 is preferably 8.0%, and more preferably in the order of 8.5%, 9.0%, 9.5%, 10.0%, 10.5%, 11.0%, 11.5%, and 12.0%. In addition, the upper limit of the content of B2O3 is preferably 20.0%, and more preferably in the order of 19.5%, 19.0%, 18.5%, 18.0%, 17.5%, 17.0%, 16.5%, 16.0%, 15.5%, and 15.0%.
B 2O 3為玻璃的網絡形成成分，具有改善玻璃的熱穩定性的作用。另外，是在網絡形成成分中，相對不會降低平均線膨脹係數α L的成分。另一方面，B 2O 3的含量多時，存在折射率nd降低之虞。因此，B 2O 3的含量較佳為上述範圍。 B2O3 is a network-forming component of glass and has the effect of improving the thermal stability of glass. In addition, it is a component that does not relatively reduce the average linear expansion coefficient αL among network-forming components. On the other hand, when the content of B2O3 is high, there is a risk that the refractive index nd will decrease. Therefore, the content of B2O3 is preferably within the above range.
在第3實施方式的光學玻璃中，Al 2O 3的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.2%、0.1%的順序更佳。另外，Al 2O 3的含量的下限較佳為0%。Al 2O 3的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the content of Al2O3 is preferably 10%, and more preferably in the order of 8%, 6%, 4 %, 2%, 1%, 0.5%, 0.2%, and 0.1%. In addition, the lower limit of the content of Al2O3 is preferably 0%. The content of Al2O3 may also be 0%.
Al 2O 3是具有改善玻璃的化學耐久性、耐候性的作用的玻璃成分，可以認為是網絡形成成分。另一方面，Al 2O 3的含量變多時，存在折射率nd降低、玻璃的熱穩定性及熔融性降低之虞。因此，Al 2O 3的含量較佳為上述範圍。 Al2O3 is a glass component that improves the chemical durability and weather resistance of glass and can be considered as a network-forming component. On the other hand, when the content of Al2O3 increases, there is a risk of lowering the refractive index nd and lowering the thermal stability and solubility of the glass . Therefore, the content of Al2O3 is preferably within the above range.
在第3實施方式的光學玻璃中，P 2O 5的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.2%、0.1%的順序更佳。另外，P 2O 5的含量的下限較佳為0%。P 2O 5的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the content of P2O5 is preferably 10%, and more preferably in the order of 8%, 6%, 4 %, 2%, 1%, 0.5%, 0.2%, and 0.1%. In addition, the lower limit of the content of P2O5 is preferably 0%. The content of P2O5 may also be 0%.
P 2O 5是降低折射率nd的成分，此外，也是降低玻璃的熱穩定性的成分。因此，P 2O 5的含量較佳為上述範圍。 P2O5 is a component that lowers the refractive index nd and also a component that lowers the thermal stability of glass. Therefore, the content of P2O5 is preferably within the above range.
在第3實施方式的光學玻璃中，Li 2O的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.2%、0.1%的順序更佳。另外，Li 2O的含量的下限較佳為0%。Li 2O的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the content of Li2O is preferably 10%, and more preferably in the order of 8%, 6%, 4%, 2%, 1%, 0.5%, 0.2%, and 0.1%. In addition, the lower limit of the content of Li2O is preferably 0%. The content of Li2O may be 0%.
Li 2O是有助於玻璃的低比重化的成分，具有改善玻璃的熔融性、並且增大平均線膨脹係數α L的作用。此外，是有助於玻璃化轉變溫度Tg的降低的成分，在精密壓製成型時有助於成型性的提高。另一方面，Li 2O的含量變多時，耐失透性、耐酸性降低。因此，Li 2O的含量較佳為上述範圍。 Li2O is a component that contributes to lowering the specific gravity of glass, improves the meltability of glass, and increases the average linear expansion coefficient αL . It is also a component that contributes to lowering the glass transition temperature Tg, and contributes to improving moldability during precision press molding. On the other hand, when the content of Li2O increases, the devitrification resistance and acid resistance decrease. Therefore, the content of Li2O is preferably within the above range.
在第3實施方式的光學玻璃中，Na 2O的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.2%、0.1%的順序更佳。另外，Na 2O的含量的下限較佳為0%。Na 2O的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the content of Na2O is preferably 10%, and more preferably in the order of 8%, 6%, 4%, 2%, 1%, 0.5%, 0.2%, and 0.1%. In addition, the lower limit of the content of Na2O is preferably 0%. The content of Na2O may be 0%.
在第3實施方式的光學玻璃中，K 2O的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.2%、0.1%的順序更佳。另外，K 2O的含量的下限較佳為0%。K 2O的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the K 2 O content is preferably 10%, more preferably 8%, 6%, 4%, 2%, 1%, 0.5%, 0.2%, and 0.1%. The lower limit of the K 2 O content is preferably 0%. The K 2 O content may be 0%.
在第3實施方式的光學玻璃中，Na 2O及K 2O的合計含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.2%、0.1%的順序更佳。另外，該合計含量的下限較佳為0%，進一步以0.001%、0.01%、0.05%的順序更佳。 In the optical glass of the third embodiment, the upper limit of the total content of Na2O and K2O is preferably 10%, more preferably 8%, 6%, 4%, 2%, 1%, 0.5%, 0.2%, 0.1%, in this order. The lower limit of the total content is preferably 0%, more preferably 0.001%, 0.01%, 0.05%, in this order.
Na 2O、K 2O均具有改善玻璃的熔融性的作用。另外，具有增大平均線膨脹係數的作用。另一方面，它們的含量變多時，熱穩定性、耐失透性、化學耐久性、耐候性降低。因此，Na 2O及K 2O的各含量及其合計含量較佳為上述範圍。 Na 2 O and K 2 O both have the effect of improving the solubility of glass. They also have the effect of increasing the average linear expansion coefficient. On the other hand, when their contents increase, thermal stability, devitrification resistance, chemical durability, and weather resistance decrease. Therefore, the contents of Na 2 O and K 2 O and their total content are preferably within the above ranges.
在第3實施方式的光學玻璃中，Cs 2O的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.2%、0.1%的順序更佳。另外，Cs 2O的含量的下限較佳為0%。Cs 2O的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the Cs 2 O content is preferably 10%, and more preferably in the order of 8%, 6%, 4%, 2%, 1%, 0.5%, 0.2%, and 0.1%. In addition, the lower limit of the Cs 2 O content is preferably 0%. The Cs 2 O content may be 0%.
Cs 2O具有改善玻璃的熔融性的作用，但含量變多時，玻璃的熱穩定性、折射率nd降低，另外，在熔解中，玻璃成分的揮發增加，存在無法得到期望的玻璃之虞。因此，Cs 2O的含量較佳為上述範圍。 Cs 2 O has the effect of improving the melting property of glass, but when the content is too high, the thermal stability and refractive index nd of the glass decrease, and the volatility of glass components increases during melting, so there is a possibility that the desired glass cannot be obtained. Therefore, the content of Cs 2 O is preferably within the above range.
在第3實施方式的光學玻璃中，Li 2O、Na 2O、K 2O及Cs 2O的合計含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.2%、0.1%的順序更佳。另外，該合計含量的下限較佳為0%。該合計含量也可以為0%。從抑制玻璃的液相溫度上升的觀點考慮，Li 2O、Na 2O、K 2O及Cs 2O的合計含量較佳設為上述範圍。 In the optical glass of the third embodiment, the upper limit of the total content of Li 2 O, Na 2 O, K 2 O and Cs 2 O is preferably 10%, and more preferably in the order of 8%, 6%, 4%, 2%, 1%, 0.5%, 0.2%, and 0.1%. In addition, the lower limit of the total content is preferably 0%. The total content may also be 0%. From the viewpoint of suppressing the increase in the liquidus temperature of the glass, the total content of Li 2 O, Na 2 O, K 2 O and Cs 2 O is preferably set to the above range.
在第3實施方式的光學玻璃中，MgO的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.2%、0.1%的順序更佳。另外，MgO的含量的下限較佳為0%。MgO的含量也可以為0%。In the optical glass of the third embodiment, the upper limit of the MgO content is preferably 10%, and more preferably in the order of 8%, 6%, 4%, 2%, 1%, 0.5%, 0.2%, and 0.1%. In addition, the lower limit of the MgO content is preferably 0%. The MgO content may also be 0%.
在第3實施方式的光學玻璃中，CaO的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.2%、0.1%的順序更佳。另外，CaO的含量的下限較佳為0%。CaO的含量也可以為0%。In the optical glass of the third embodiment, the upper limit of the CaO content is preferably 10%, and more preferably in the order of 8%, 6%, 4%, 2%, 1%, 0.5%, 0.2%, and 0.1%. In addition, the lower limit of the CaO content is preferably 0%. The CaO content may also be 0%.
在第3實施方式的光學玻璃中，SrO的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.4%、0.3%的順序更佳。另外，SrO的含量的下限較佳為0%，進一步以0.05%、0.10%、0.15%、0.20%的順序更佳。In the optical glass of the third embodiment, the upper limit of the SrO content is preferably 10%, and more preferably in the order of 8%, 6%, 4%, 2%, 1%, 0.5%, 0.4%, and 0.3%. In addition, the lower limit of the SrO content is preferably 0%, and more preferably in the order of 0.05%, 0.10%, 0.15%, and 0.20%.
在第3實施方式的光學玻璃中，MgO、CaO及SrO的合計含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.4%、0.3%的順序更佳。另外，該合計含量的下限較佳為0%，進一步以0.05%、0.10%、0.15%、0.20%的順序更佳。該合計含量也可以為0%。In the optical glass of the third embodiment, the upper limit of the total content of MgO, CaO and SrO is preferably 10%, and more preferably in the order of 8%, 6%, 4%, 2%, 1%, 0.5%, 0.4%, and 0.3%. In addition, the lower limit of the total content is preferably 0%, and more preferably in the order of 0.05%, 0.10%, 0.15%, and 0.20%. The total content may also be 0%.
MgO、CaO、SrO均為具有改善玻璃的熔融性的作用的玻璃成分，也具有使平均線膨脹係數較大的作用。然而，這些玻璃成分的含量變多時，玻璃的熱穩定性及耐失透性降低。因此，這些玻璃成分的各含量及合計含量較佳為上述範圍。MgO, CaO, and SrO are glass components that improve the melting property of glass and also have the effect of increasing the average linear expansion coefficient. However, when the content of these glass components increases, the thermal stability and devitrification resistance of the glass decrease. Therefore, the content of each of these glass components and the total content are preferably within the above range.
在第3實施方式的光學玻璃中，BaO的含量的下限較佳為20%，進一步以21%、22%、23%、24%、25%、26%、27%、28%、29%、30%、31%的順序更佳。另外，BaO的含量的上限較佳為45%，進一步以44%、43%、42%、41%、40%、39%、38%、37%、36%、35%、34%的順序更佳。In the optical glass of the third embodiment, the lower limit of the BaO content is preferably 20%, and more preferably in the order of 21%, 22%, 23%, 24%, 25%, 26%, 27%, 28%, 29%, 30%, and 31%. In addition, the upper limit of the BaO content is preferably 45%, and more preferably in the order of 44%, 43%, 42%, 41%, 40%, 39%, 38%, 37%, 36%, 35%, and 34%.
BaO是具有增加平均線膨脹係數α L的作用、且不損害高折射率/低色散特性的玻璃成分。藉由將BaO的含量設為上述範圍，可得到高折射率/低色散、且改善了平均線膨脹係數α L的光學玻璃。另一方面，BaO的含量過多時，存在玻璃的熱穩定性降低、玻璃發生失透之虞。 BaO is a glass component that has the effect of increasing the average linear expansion coefficient α L without impairing the high refractive index/low dispersion characteristics. By setting the BaO content within the above range, an optical glass with high refractive index/low dispersion and improved average linear expansion coefficient α L can be obtained. On the other hand, when the BaO content is too high, there is a risk that the thermal stability of the glass is reduced and the glass may become devitrified.
在第3實施方式的光學玻璃中，SiO 2及B 2O 3的合計含量的上限較佳為30%，進一步以29%、28%、27%、26%、25%、24%、23%、22%、21%、20%的順序更佳。另外，該合計含量的下限較佳為13%，進一步以14%、15%、16%、17%、18%的順序更佳。 In the optical glass of the third embodiment, the upper limit of the total content of SiO2 and B2O3 is preferably 30%, and more preferably in the order of 29%, 28%, 27%, 26%, 25%, 24%, 23%, 22%, 21%, and 20%. In addition, the lower limit of the total content is preferably 13%, and more preferably in the order of 14%, 15%, 16%, 17%, and 18%.
從保持玻璃的穩定性、並且抑制折射率的降低的觀點考慮，SiO 2及B 2O 3的合計含量較佳設為上述範圍。 From the viewpoint of maintaining the stability of the glass and suppressing the decrease in the refractive index, the total content of SiO 2 and B 2 O 3 is preferably within the above range.
在第3實施方式的光學玻璃中，BaO的含量與SiO 2及B 2O 3的合計含量的質量比[BaO/(SiO 2+B 2O 3)]的上限較佳為3.00，進一步以2.80、2.60、2.40、2.20、2.00、1.80、1.70的順序更佳。另外，該質量比的下限較佳為0.60，進一步以0.80、0.90、1.00、1.10、1.20、1.30的順序更佳。 In the optical glass of the third embodiment, the upper limit of the mass ratio of the content of BaO to the total content of SiO2 and B2O3 [BaO/( SiO2 + B2O3 ) ] is preferably 3.00, more preferably in the order of 2.80, 2.60, 2.40, 2.20, 2.00, 1.80, and 1.70. The lower limit of the mass ratio is preferably 0.60, more preferably in the order of 0.80, 0.90, 1.00, 1.10, 1.20, and 1.30.
從得到可保持玻璃的穩定性、並且平均線膨脹係數α L大的玻璃的觀點考慮，該質量比較佳設為上述範圍。 From the perspective of obtaining glass that can maintain glass stability and has a large average linear expansion coefficient αL , the mass is preferably set to the above range.
在第3實施方式的光學玻璃中，ZnO的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.4%、0.3%、0.2%、0.1%、0.05%、0.03%、0.02%、0.01%的順序更佳。另外，ZnO的含量的下限較佳為0%。ZnO的含量也可以為0%。In the optical glass of the third embodiment, the upper limit of the content of ZnO is preferably 10%, and more preferably in the order of 8%, 6%, 4%, 2%, 1%, 0.5%, 0.4%, 0.3%, 0.2%, 0.1%, 0.05%, 0.03%, 0.02%, and 0.01%. In addition, the lower limit of the content of ZnO is preferably 0%. The content of ZnO may also be 0%.
ZnO是具有改善玻璃的熔融性的作用的玻璃成分。然而，ZnO的含量過多時，存在玻璃的比重增大、平均線膨脹係數α L降低之虞。另外，也存在損害玻璃的低色散性之虞。此外，還存在玻璃化轉變溫度Tg降低之虞。因此，ZnO的含量較佳為上述範圍。 ZnO is a glass component that improves the melting property of glass. However, when the content of ZnO is too high, there is a risk that the specific gravity of the glass increases and the average linear expansion coefficient α L decreases. In addition, there is also a risk that the low dispersion of the glass is damaged. In addition, there is also a risk that the glass transition temperature Tg decreases. Therefore, the content of ZnO is preferably within the above range.
在第3實施方式的光學玻璃中，La 2O 3的含量的下限較佳為15%，進一步以16%、17%、18%、19%、20%、21%、22%的順序更佳。另外，La 2O 3的含量的上限較佳為40%，進一步以39%、38%、37%、36%、35%、34%、33%、32%、31%、30%、29%、28%的順序更佳。 In the optical glass of the third embodiment, the lower limit of the content of La2O3 is preferably 15%, and more preferably in the order of 16%, 17%, 18%, 19%, 20%, 21%, and 22%. In addition, the upper limit of the content of La2O3 is preferably 40%, and more preferably in the order of 39%, 38%, 37%, 36%, 35%, 34%, 33%, 32%, 31%, 30%, 29%, and 28%.
La 2O 3是具有抑制阿貝數νd的減少且提高折射率的作用的玻璃成分。因此，藉由將La 2O 3的含量設為上述範圍，可得到高折射率/低色散、抑制了平均線膨脹係數α L的降低、並且抑制了相對折射率的溫度係數(dn/dT)的增大的光學玻璃。 La2O3 is a glass component that has the effect of suppressing the decrease of the Abbe number νd and increasing the refractive index. Therefore, by setting the content of La2O3 to the above range, an optical glass with high refractive index/low dispersion, suppressed decrease in the average linear expansion coefficient αL , and suppressed increase in the temperature coefficient of relative refractive index (dn/dT) can be obtained.
在第3實施方式的光學玻璃中，Gd 2O 3的含量的上限較佳為20%，進一步以15%、10%、5%、4%、3%、2%、1%、0.5%的順序更佳。另外，Gd 2O 3的含量的下限較佳為0%。Gd 2O 3的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the content of Gd2O3 is preferably 20%, and more preferably in the order of 15%, 10%, 5%, 4 %, 3%, 2%, 1%, and 0.5%. In addition, the lower limit of the content of Gd2O3 is preferably 0%. The content of Gd2O3 may also be 0%.
Gd 2O 3為高折射/低色散、且能夠抑制平均線膨脹係數α L的降低的成分，但在大量導入BaO的本實施方式的玻璃中，Gd 2O 3的含量變得過多時，玻璃的熱穩定性及耐失透性降低，在製造中玻璃變得容易失透。另外，Gd 2O 3的含量變得過多時，玻璃的比重增大，因而不佳。另外，從原料成本削減的觀點考慮也不利。因此，Gd 2O 3的含量較佳為上述範圍。 Gd2O3 is a component with high refractive index and low dispersion and can suppress the decrease of the average linear expansion coefficient αL . However, in the glass of the present embodiment in which a large amount of BaO is introduced, when the content of Gd2O3 becomes too high, the thermal stability and devitrification resistance of the glass decrease, and the glass becomes easy to devitrify during manufacturing. In addition, when the content of Gd2O3 becomes too high, the specific gravity of the glass increases , which is not good. In addition, it is not good from the perspective of reducing the cost of raw materials. Therefore, the content of Gd2O3 is preferably within the above range.
在第3實施方式的光學玻璃中，Y 2O 3的含量的下限較佳為5%，進一步以6%、7%、8%、9%、10%、11%、12%、13%、14%的順序更佳。另外，Y 2O 3的含量的上限較佳為25%，進一步以24%、23%、22%、21%、20%、19%的順序更佳。 In the optical glass of the third embodiment, the lower limit of the content of Y2O3 is preferably 5%, and more preferably in the order of 6%, 7%, 8%, 9%, 10%, 11%, 12%, 13%, and 14%. In addition, the upper limit of the content of Y2O3 is preferably 25%, and more preferably in the order of 24%, 23%, 22%, 21%, 20 % , and 19%.
Y 2O 3是具有抑制阿貝數νd的減少、且提高折射率的作用的成分。 另外，在導入了比較多的鹼金屬成分、鹼土金屬成分中的BaO或SrO的本實施方式的玻璃中，Y 2O 3是對於抑制平均線膨脹係數α L的降低、賦予高折射低色散特性而言有效的成分。另外，還具有改善玻璃的化學耐久性、耐候性、提高玻璃化轉變溫度的作用。另一方面，Y 2O 3的含量變得過多時，存在玻璃的熱穩定性及耐失透性降低之虞。因此，Y 2O 3的含量較佳為上述範圍。 Y2O3 is a component that has the effect of suppressing the decrease of the Abbe number νd and increasing the refractive index. In addition, in the glass of the present embodiment that introduces a relatively large amount of BaO or SrO among the alkali metal components and alkaline earth metal components, Y2O3 is an effective component for suppressing the decrease of the mean linear expansion coefficient αL and imparting high refractive and low dispersion characteristics. In addition, it also has the effect of improving the chemical durability and weather resistance of the glass and increasing the glass transition temperature. On the other hand, when the content of Y2O3 becomes too much, there is a risk that the thermal stability and devitrification resistance of the glass will be reduced. Therefore, the content of Y2O3 is preferably within the above range.
在第3實施方式的光學玻璃中，ZrO 2的含量的上限較佳為10%，進一步以9%、8%、7%、6%、5%、4%、3%、2.5%的順序更佳。另外，ZrO 2的含量的下限較佳為0%，進一步以0.005%、0.01%、0.05%、0.1%、0.5%、1.0%、1.5%、2.0%的順序更佳。ZrO 2的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the content of ZrO2 is preferably 10%, and more preferably in the order of 9%, 8%, 7%, 6%, 5%, 4%, 3%, and 2.5%. In addition, the lower limit of the content of ZrO2 is preferably 0%, and more preferably in the order of 0.005%, 0.01%, 0.05%, 0.1%, 0.5%, 1.0%, 1.5%, and 2.0%. The content of ZrO2 may also be 0%.
ZrO 2是具有提高折射率的作用的成分，藉由適量含有ZrO 2，還具有改善玻璃的熱穩定性的作用。然而，ZrO 2除了是使平均線膨脹係數α L較小的成分以外，也是增大相對折射率的溫度係數(dn/dT)的溫度依賴性的成分。另外，其含量過多時，存在熱穩定性顯著降低之虞。因此，ZrO 2的含量較佳為上述範圍。 ZrO 2 is a component that has the effect of increasing the refractive index. By containing an appropriate amount of ZrO 2 , it also has the effect of improving the thermal stability of the glass. However, ZrO 2 is not only a component that makes the average linear expansion coefficient α L smaller, but also a component that increases the temperature dependence of the temperature coefficient of relative refractive index (dn/dT). In addition, when its content is too high, there is a risk that the thermal stability will be significantly reduced. Therefore, the content of ZrO 2 is preferably within the above range.
在第3實施方式的光學玻璃中，TiO 2的含量的上限較佳為15%，進一步以14%、13%、12%、11%、10%、9%、8%、7%、6%的順序更佳。另外，TiO 2的含量的下限較佳為0%，進一步以1%、2%、3%、4%、5%的順序更佳。TiO 2的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the content of TiO2 is preferably 15%, and more preferably in the order of 14%, 13%, 12%, 11%, 10%, 9%, 8%, 7%, and 6%. In addition, the lower limit of the content of TiO2 is preferably 0%, and more preferably in the order of 1%, 2%, 3%, 4%, and 5%. The content of TiO2 may also be 0%.
TiO 2是具有提高折射率的作用的成分，藉由適量含有TiO 2，還具有改善玻璃的熱穩定性的作用。另一方面，TiO 2的含量過多時，除了存在平均線膨脹係數α L降低之虞以外，還存在阿貝數νd降低之虞，另外還存在玻璃的著色變強、進而熔融性變差之虞。因此，TiO 2的含量較佳為上述範圍。 TiO 2 is a component that has the effect of increasing the refractive index. By containing an appropriate amount of TiO 2 , it also has the effect of improving the thermal stability of the glass. On the other hand, when the content of TiO 2 is too high, in addition to the possibility of reducing the average linear expansion coefficient α L , there is also the possibility of reducing the Abbe number νd, and there is also the possibility of increasing the coloring of the glass and further deteriorating the meltability. Therefore, the content of TiO 2 is preferably within the above range.
在第3實施方式的光學玻璃中，Nb 2O 5的含量的上限較佳為20%，進一步以19%、18%、17%、16%、15%、14%、13%、12%、11%、10%、5%、3%、2%、1%的順序更佳。另外，Nb 2O 5的含量的下限較佳為0%，進一步以0.001%、0.003%、0.005%、0.010%、0.050%、0.080%、0.100%的順序更佳。Nb 2O 5的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the content of Nb2O5 is preferably 20%, and more preferably in the order of 19%, 18%, 17%, 16%, 15%, 14%, 13%, 12%, 11%, 10%, 5%, 3%, 2%, and 1%. In addition, the lower limit of the content of Nb2O5 is preferably 0%, and more preferably in the order of 0.001%, 0.003%, 0.005%, 0.010%, 0.050%, 0.080%, and 0.100%. The content of Nb2O5 may also be 0%.
Nb 2O 5是具有提高折射率的作用的成分，藉由適量含有Nb 2O 5，還具有改善玻璃的熱穩定性的作用。另一方面，Nb 2O 5的含量過多時，除了存在平均線膨脹係數α L降低之虞以外，還存在玻璃的著色變強之虞。因此，Nb 2O 5的含量較佳為上述範圍。 Nb2O5 is a component that has the effect of increasing the refractive index. When Nb2O5 is contained in an appropriate amount , it also has the effect of improving the thermal stability of the glass. On the other hand, when the content of Nb2O5 is too high, there is a possibility that the average linear expansion coefficient αL is reduced and the coloring of the glass is increased. Therefore, the content of Nb2O5 is preferably within the above range.
在第3實施方式的光學玻璃中，WO 3的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.1%的順序更佳。另外，WO 3的含量的下限較佳為0%。WO 3的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the content of WO 3 is preferably 10%, and more preferably in the order of 8%, 6%, 4%, 2%, 1%, 0.5%, and 0.1%. In addition, the lower limit of the content of WO 3 is preferably 0%. The content of WO 3 may also be 0%.
WO 3對其它高色散成分具有降低玻璃化轉變溫度Tg的作用，因此，將玻璃軟化成型時，尤其是實施精密壓製時，能夠出於降低成型溫度以保護成型模具、其保護膜、成型機的目的而導入WO 3。另一方面，從提高玻璃的透射率的觀點及抑制玻璃的相對折射率的溫度係數(dn/dT)的上升的觀點考慮，WO 3的含量較佳為上述範圍。 WO 3 has the effect of lowering the glass transition temperature Tg of other high-dispersion components. Therefore, when softening and molding glass, especially when precision pressing is performed, WO 3 can be introduced for the purpose of lowering the molding temperature to protect the molding mold, its protective film, and the molding machine. On the other hand, from the perspective of improving the transmittance of the glass and suppressing the increase in the temperature coefficient of the relative refractive index (dn/dT) of the glass, the content of WO 3 is preferably within the above range.
在第3實施方式的光學玻璃中，Bi 2O 3的含量的上限較佳為10%，進一步以8%、6%、4%、2%、1%、0.5%、0.1%的順序更佳。另外，Bi 2O 3的含量的下限較佳為0%。Bi 2O 3的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the content of Bi2O3 is preferably 10%, and more preferably in the order of 8%, 6%, 4 %, 2%, 1%, 0.5%, and 0.1%. In addition, the lower limit of the content of Bi2O3 is preferably 0%. The content of Bi2O3 may also be 0%.
Bi 2O 3是提高折射率nd、但降低阿貝數νd的成分。另外，也是容易增大玻璃的著色的成分。因此，Bi 2O 3的含量較佳為上述範圍。 Bi 2 O 3 is a component that increases the refractive index nd but decreases the Abbe number νd. In addition, it is also a component that tends to increase the coloring of the glass. Therefore, the content of Bi 2 O 3 is preferably within the above range.
在第3實施方式的光學玻璃中，Ta 2O 5的含量的上限較佳為20%，進一步以15%、13%、10%、5%、3%、1%的順序更佳。另外，Ta 2O 5的含量的下限較佳為0%。Ta 2O 5的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the content of Ta2O5 is preferably 20%, and more preferably in the order of 15%, 13%, 10 %, 5%, 3%, and 1%. In addition, the lower limit of the content of Ta2O5 is preferably 0%. The content of Ta2O5 may also be 0%.
Ta 2O 5是具有改善玻璃的熱穩定性及耐失透性的作用的玻璃成分。另一方面，Ta 2O 5使折射率上升，使玻璃高色散化。另外，Ta 2O 5的含量變多時，玻璃的熱穩定性降低，將玻璃熔融時，變得容易發生玻璃原料的熔融殘留。另外，Ta 2O 5是相對降低平均線膨脹係數α L的成分。因此，Ta 2O 5的含量較佳為上述範圍。此外，Ta 2O 5是與其它玻璃成分相比非常昂貴的成分，Ta 2O 5的含量變多時，玻璃的生產成本增大。此外，Ta 2O 5的分子量比其它玻璃成分大，因此，會增大玻璃的比重，結果會增大光學元件的重量。 Ta 2 O 5 is a glass component that improves the thermal stability and resistance to devitrification of glass. On the other hand, Ta 2 O 5 increases the refractive index and makes the glass highly dispersed. In addition, when the content of Ta 2 O 5 increases, the thermal stability of the glass decreases, and when the glass is melted, it becomes easy to produce melt residues of the glass raw materials. In addition, Ta 2 O 5 is a component that relatively reduces the average linear expansion coefficient α L. Therefore, the content of Ta 2 O 5 is preferably within the above range. In addition, Ta 2 O 5 is a very expensive component compared to other glass components. When the content of Ta 2 O 5 increases, the production cost of the glass increases. In addition, the molecular weight of Ta 2 O 5 is larger than that of other glass components, so it will increase the specific gravity of the glass , resulting in an increase in the weight of the optical element.
在第3實施方式的光學玻璃中，Sc 2O 3的含量的上限較佳為2%。另外，Sc 2O 3的含量的下限較佳為0%。 In the optical glass of the third embodiment, the upper limit of the content of Sc 2 O 3 is preferably 2%. In addition, the lower limit of the content of Sc 2 O 3 is preferably 0%.
在第3實施方式的光學玻璃中，HfO 2的含量的上限較佳為2%。另外，HfO 2的含量的下限較佳為0%。 In the optical glass of the third embodiment, the upper limit of the content of HfO 2 is preferably 2%. In addition, the lower limit of the content of HfO 2 is preferably 0%.
Sc 2O 3、HfO 2均具有提高折射率nd的作用，而且是昂貴的成分。因此，Sc 2O 3、HfO 2的各含量較佳為上述範圍。 Sc 2 O 3 and HfO 2 both have the function of increasing the refractive index nd and are expensive components. Therefore, the contents of Sc 2 O 3 and HfO 2 are preferably within the above ranges.
在第3實施方式的光學玻璃中，Lu 2O 3的含量的上限較佳為2%。另外，Lu 2O 3的含量的下限較佳為0%。 In the optical glass of the third embodiment, the upper limit of the content of Lu 2 O 3 is preferably 2%. In addition, the lower limit of the content of Lu 2 O 3 is preferably 0%.
Lu 2O 3具有提高折射率nd的作用。另外，由於其分子量大，所以也是增加玻璃的比重的玻璃成分。因此，Lu 2O 3的含量較佳為上述範圍。 Lu 2 O 3 has the effect of increasing the refractive index nd. In addition, due to its large molecular weight, it is also a glass component that increases the specific gravity of glass. Therefore, the content of Lu 2 O 3 is preferably within the above range.
在第3實施方式的光學玻璃中，GeO 2的含量的上限較佳為2%。另外，GeO 2的含量的下限較佳為0%。 In the optical glass of the third embodiment, the upper limit of the content of GeO2 is preferably 2%. In addition, the lower limit of the content of GeO2 is preferably 0%.
GeO 2具有提高折射率nd的作用，另外，其在通常使用的玻璃成分中是明顯昂貴的成分。因此，從降低玻璃的製造成本的觀點考慮，GeO 2的含量較佳為上述範圍。 GeO 2 has the effect of increasing the refractive index nd, and is a significantly expensive component in the commonly used glass components. Therefore, from the perspective of reducing the manufacturing cost of glass, the content of GeO 2 is preferably within the above range.
在第3實施方式的光學玻璃中，La 2O 3的含量的上限較佳為2%。另外，La 2O 3的含量的下限較佳為0%。La 2O 3的含量也可以為0%。 In the optical glass of the third embodiment, the upper limit of the content of La 2 O 3 is preferably 2%. In addition, the lower limit of the content of La 2 O 3 is preferably 0%. The content of La 2 O 3 may also be 0%.
La 2O 3的含量變多時，玻璃的熱穩定性及耐失透性降低，在製造中玻璃變得容易失透。因此，從抑制熱穩定性及耐失透性的降低的觀點考慮，La 2O 3的含量較佳為上述範圍。 When the content of La2O3 increases, the thermal stability and devitrification resistance of the glass decrease, and the glass becomes easy to devitrify during production. Therefore, from the viewpoint of suppressing the decrease in thermal stability and devitrification resistance, the content of La2O3 is preferably within the above range.
在第3實施方式的光學玻璃中，Yb 2O 3的含量的上限較佳為2%。另外，Yb 2O 3的含量的下限較佳為0%。 In the optical glass of the third embodiment, the upper limit of the content of Yb 2 O 3 is preferably 2%. In addition, the lower limit of the content of Yb 2 O 3 is preferably 0%.
Yb 2O 3的含量過多時，存在玻璃的熱穩定性及耐失透性降低之虞。另外，Yb 2O 3在通常使用的玻璃成分中是昂貴的成分。從防止玻璃的熱穩定性的降低、抑制比重的增大的觀點考慮，以及從抑制玻璃的製造成本的觀點考慮，Yb 2O 3的含量較佳為上述範圍。 When the content of Yb2O3 is too high, the thermal stability and devitrification resistance of the glass may be reduced. In addition, Yb2O3 is an expensive component in the glass components generally used. From the viewpoint of preventing the reduction of the thermal stability of the glass and suppressing the increase of the specific gravity, and from the viewpoint of suppressing the production cost of the glass, the content of Yb2O3 is preferably within the above range.
第3實施方式的光學玻璃較佳主要由上述的玻璃成分SiO 2、B 2O 3、Al 2O 3、P 2O 5、Li 2O、Na 2O、K 2O、Cs 2O、MgO、CaO、SrO、BaO、ZnO、La 2O 3、Gd 2O 3、Y 2O 3、ZrO 2、TiO 2、Nb 2O 5、WO 3、Bi 2O 3、Ta 2O 5、Sc 2O 3、HfO 2、Lu 2O 3、GeO 2及Yb 2O 3構成，上述的玻璃成分的合計含量較佳為95%以上、更佳較佳為98%以上、進一步較佳為99%以上、更進一步較佳為99.5%以上。 The optical glass of the third embodiment is preferably mainly composed of the above-mentioned glass components SiO2 , B2O3 , Al2O3 , P2O5 , Li2O , Na2O , K2O , Cs2O , MgO , CaO, SrO , BaO, ZnO, La2O3 , Gd2O3 , Y2O3, ZrO2 , TiO2 , Nb2O5 , WO3 , Bi2O3 , Ta2O5 , Sc2O3 , HfO2 , Lu2O3 , GeO2 and Yb2O3 . 3 , the total content of the above-mentioned glass components is preferably 95% or more, more preferably 98% or more, further preferably 99% or more, and further preferably 99.5% or more.
在第3實施方式的光學玻璃中，TeO 2的含量的上限較佳為2%。另外，TeO 2的含量的下限較佳為0%。 In the optical glass of the third embodiment, the upper limit of the content of TeO2 is preferably 2%. In addition, the lower limit of the content of TeO2 is preferably 0%.
TeO 2具有毒性，因此，較佳減少TeO 2的含量。因此，TeO 2的含量較佳為上述範圍。 TeO 2 is toxic, so it is better to reduce the content of TeO 2. Therefore, the content of TeO 2 is preferably within the above range.
在第3實施方式的光學玻璃中，氟(F)的含量較佳為3%以下，其上限以1%、0.5%、0.3%的順序更佳。F的含量少的情況為佳，其下限較佳為0%。F的含量也可以為0%。另外，較佳實質上不含氟(F)。In the optical glass of the third embodiment, the content of fluorine (F) is preferably 3% or less, and the upper limit is preferably 1%, 0.5%, and 0.3% in that order. The less the content of F, the better, and the lower limit is preferably 0%. The content of F may also be 0%. In addition, it is preferred that fluorine (F) is not substantially contained.
藉由將F的含量設為上述範圍，能夠抑制玻璃在熔解中的揮發，能夠抑制折射率的變動、波筋。By setting the F content within the above range, volatility of the glass during melting can be suppressed, and fluctuations in the refractive index and striae can be suppressed.
需要說明的是，第3實施方式的光學玻璃較佳基本上由上述玻璃成分構成，也可以在不妨礙本發明的作用效果的範圍中含有其它成分。另外，在本發明中，不排除含有不可避免的雜質。It should be noted that the optical glass of the third embodiment is preferably basically composed of the above-mentioned glass components, and may contain other components within the scope that does not hinder the effects of the present invention. In addition, in the present invention, it is not excluded to contain inevitable impurities.
＜其它成分組成＞ Pb、As、Cd、Tl、Be、Se均具有毒性。因此，本實施方式的光學玻璃較佳不含有這些元素作為玻璃成分。 <Other components> Pb, As, Cd, Tl, Be, and Se are all toxic. Therefore, the optical glass of this embodiment preferably does not contain these elements as glass components.
U、Th、Ra均為放射性元素。因此，本實施方式的光學玻璃較佳不含有這些元素作為玻璃成分。U, Th, and Ra are all radioactive elements. Therefore, the optical glass of this embodiment preferably does not contain these elements as glass components.
V、Cr、Mn、Fe、Co、Ni、Cu、Pr、Nd、Pm、Sm、Eu、Tb、Dy、Ho、Er、Tm會增大玻璃的著色，成為螢光的產生源。因此，本實施方式的光學玻璃較佳不含有這些元素作為玻璃成分。V, Cr, Mn, Fe, Co, Ni, Cu, Pr, Nd, Pm, Sm, Eu, Tb, Dy, Ho, Er, and Tm increase the coloring of the glass and become a source of fluorescence. Therefore, the optical glass of the present embodiment preferably does not contain these elements as glass components.
Sb(Sb 2O 3)、Ce(CeO 2)是作為澄清劑發揮功能的可任意添加的元素。其中，Sb(Sb 2O 3)是澄清效果大的澄清劑。 Sb (Sb 2 O 3 ) and Ce (CeO 2 ) are elements that can be added arbitrarily and function as fining agents. Among them, Sb (Sb 2 O 3 ) is a fining agent with a large fining effect.
Sb 2O 3的含量以外加比例表示。即，將Sb 2O 3及CeO 2以外的全部玻璃成分的合計含量設為100質量%時的Sb 2O 3的含量較佳小於1質量%、更佳小於0.1質量%。進一步以小於0.05質量%、小於0.03質量%、小於0.02質量%、小於0.01%的順序為佳。Sb 2O 3的含量也可以為0質量%。 The content of Sb2O3 is expressed as an additional ratio. That is, when the total content of all glass components other than Sb2O3 and CeO2 is set to 100 mass%, the content of Sb2O3 is preferably less than 1 mass %, more preferably less than 0.1 mass %. It is further preferably less than 0.05 mass%, less than 0.03 mass%, less than 0.02 mass%, and less than 0.01% in this order. The content of Sb2O3 may also be 0 mass%.
CeO 2的含量也以外加比例表示。即，將CeO 2、Sb 2O 3以外的全部玻璃成分的合計含量設為100質量%時的CeO 2的含量較佳小於2質量%、更佳小於1質量%、進一步較佳小於0.5質量%、更進一步較佳小於0.1質量%的範圍。CeO 2的含量也可以為0質量%。藉由將CeO 2的含量設為上述範圍，能夠改善玻璃的澄清性。 The content of CeO 2 is also expressed as an additional ratio. That is, when the total content of all glass components other than CeO 2 and Sb 2 O 3 is set to 100 mass %, the content of CeO 2 is preferably less than 2 mass %, more preferably less than 1 mass %, further preferably less than 0.5 mass %, and further preferably less than 0.1 mass %. The content of CeO 2 may also be 0 mass %. By setting the content of CeO 2 to the above range, the clarity of the glass can be improved.
在第3實施方式的光學玻璃中，可以將玻璃特性設為與第1實施方式同樣。In the optical glass of the third embodiment, the glass properties can be set to be the same as those of the first embodiment.
可以將第3實施方式的光學玻璃的製造及光學元件等的製造設為與第1實施方式同樣。The production of the optical glass and the production of the optical elements, etc., of the third embodiment can be made the same as those of the first embodiment.
以下，對第4實施方式詳細地進行說明。The fourth implementation method is described in detail below.
第4實施方式 第4實施方式的光學玻璃如下：以氧化物基準計，將玻璃成分SiO 2、B 2O 3、Al 2O 3、Li 2O、Na 2O、K 2O、Cs 2O、MgO、CaO、SrO、BaO、ZnO、La 2O 3、Gd 2O 3、Y 2O 3、ZrO 2、TiO 2、Nb 2O 5、WO 3及Bi 2O 3的以質量%表示的含量分別設為C(SiO 2)、C(B 2O 3)、C(Al 2O 3)、C(Li 2O)、C(Na 2O)、C(K 2O)、C(Cs 2O)、C(MgO)、C(CaO)、C(SrO)、C(BaO)、C(ZnO)、C(La 2O 3)、C(Gd 2O 3)、C(Y 2O 3)、C(ZrO 2)、C(TiO 2)、C(Nb 2O 5)、C(WO 3)及C(Bi 2O 3)， 將SiO 2、BO 1.5、AlO 1.5、LiO 0.5、NaO 0.5、KO 0.5、CsO 0.5、MgO、CaO、SrO、BaO、ZnO、LaO 1.5、GdO 1.5、YO 1.5、ZrO 2、TiO 2、NbO 2.5、WO 3及BiO 1.5的各化學式量分別設為M(SiO 2)、M(BO 1.5)、M(AlO 1.5)、M(LiO 0.5)、M(NaO 0.5)、M(KO 0.5)、M(CsO 0.5)、M(MgO)、M(CaO)、M(SrO)、M(BaO)、M(ZnO)、M(LaO 1.5)、M(GdO 1.5)、M(YO 1.5)、M(ZrO 2)、M(TiO 2)、M(NbO 2.5)、M(WO 3)及M(BiO 1.5)， 設定A1＝{C(B 2O 3)/M(BO 1.5)}/{C(B 2O 3)/M(BO 1.5)+C(SiO 2)/M(SiO 2)}、 B1＝{C(BaO)/M(BaO)+C(SrO)/M(SrO)}/{C(Li 2O)/M(LiO 0.5)+C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(Cs 2O)/M(CsO 0.5)+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}、 C1＝{C(BaO)/M(BaO)+C(Li 2O)/M(LiO 0.5)}/{C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(SiO 2)/M(SiO 2)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)}、 D1＝C(Gd 2O 3)+C(ZnO)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)+C(ZrO 2)、 E1＝{C(La 2O 3)+C(Gd 2O 3)+C(Y 2O 3)}/{C(SiO 2)+C(B 2O 3)+C(Al 2O 3)}、 G1＝C(BaO)/M(BaO)+C(La 2O 3)/M(LaO 1.5)+C(Li 2O)/M(LiO 0.5)+C(Y 2O 3)/M(YO 1.5)時， A1為1/3以上， B1為0.62以上， C1為8/9以上， D1為13.50以下， E1為1.25以上， G1為0.47以上。 Fourth Embodiment The optical glass of the fourth embodiment is as follows: On an oxide basis, the contents of glass components SiO 2 , B 2 O 3 , Al 2 O 3 , Li 2 O , Na 2 O, K 2 O, Cs 2 O, MgO, CaO, SrO, BaO, ZnO, La 2 O 3 , Gd 2 O 3 , Y 2 O 3 , ZrO 2 , TiO 2 , Nb 2 O 5 , WO 3 and Bi 2 O 3, expressed in mass %, are respectively C(SiO 2 ), C(B 2 O 3 ), C(Al 2 O 3 ), C(Li 2 O ), C(Na 2 O ), C(K 2 O ), C(Cs 2 O ), C(MgO ), C(CaO ), C(SrO ), C(BaO ), C(ZnO ), C(La 2 O 3 ), C(Gd 2 O 3 ), C(Y 2 O 3 ), C(ZrO 2 ), C(TiO 2 ), C(Nb 2 O 5 ), C(WO 3 ) and C(Bi 2 O 3 ), and the chemical formula weights of SiO 2 , BO 1.5 , AlO 1.5 , LiO 0.5 , NaO 0.5 , KO 0.5 , CsO 0.5 , MgO, CaO, SrO, BaO, ZnO, LaO 1.5 , GdO 1.5 , YO 1.5 , ZrO 2 , TiO 2 , NbO 2.5 , WO 3 and BiO 1.5 are respectively designated M(SiO 2 ), M(BO 1.5 ), M(AlO 1.5 ), M(LiO 0.5 ), M(NaO 0.5 ), M(KO 0.5 ), M(CsO 0.5 ), M(MgO), M(CaO), M(SrO), M(BaO), M(ZnO), M(LaO 1.5 ), M(GdO 1.5 ), M(YO 1.5 ), M(ZrO 2 ), M(TiO 2 ), M(NbO 2.5 ) , M(WO 3 ) and M(BiO 1.5 ), set A1={C(B 2 O 3 )/M(BO 1.5 )}/{C(B 2 O 3 )/M(BO 1.5 )+C(SiO 2 )/M(SiO 2 )}, B1={C(BaO)/M(BaO)+C(SrO)/M(SrO)}/{C(Li 2 C1 ={C( BaO )/M( BaO )+C(Li 2 O)/M(LiO 0.5 )}/{C(Na 2 O)/M(NaO 0.5 )+C(K 2 O)/M(KO 0.5 ) +C(SiO 2 )/M(SiO 2 )+C ( TiO 2 ) / M(TiO 2 ) + C(Nb 2 O 5 )/M(NbO 2.5 )+C(WO 3 )/M(WO 3 )}, D1=C(Gd 2 O 3 )+C(ZnO)+C(TiO 2 )+C(Nb 2 O 5 )+C(WO 3 )+C(ZrO 2 ), E1={C(La 2 O 3 )+C(Gd 2 O 3 )+C(Y 2 O 3 )}/{C( SiO 2 )+C(B 2 O 3 )+C(Al 2 O 3 )}, G1=C(BaO)/M(BaO)+C(La 2 O 3 )/M(LaO 1.5 )+C(Li 2 O)/M(LiO 0.5 )+C(Y 2 O 3 )/M(YO 1.5 ), A1 is above 1/3, B1 is above 0.62, C1 is above 8/9, D1 is below 13.50, E1 is above 1.25, and G1 is above 0.47.
在第4實施方式中，以氧化物基準計，將玻璃成分SiO 2、B 2O 3、Al 2O 3、Li 2O、Na 2O、K 2O、Cs 2O、MgO、CaO、SrO、BaO、ZnO、La 2O 3、Gd 2O 3、Y 2O 3、ZrO 2、TiO 2、Nb 2O 5、WO 3及Bi 2O 3的以質量%表示的含量分別設為C(SiO 2)、C(B 2O 3)、C(Al 2O 3)、C(Li 2O)、C(Na 2O)、C(K 2O)、C(Cs 2O)、C(MgO)、C(CaO)、C(SrO)、C(BaO)、C(ZnO)、C(La 2O 3)、C(Gd 2O 3)、C(Y 2O 3)、C(ZrO 2)、C(TiO 2)、C(Nb 2O 5)、C(WO 3)及C(Bi 2O 3)。 In the fourth embodiment, the contents of the glass components SiO 2 , B 2 O 3 , Al 2 O 3 , Li 2 O, Na 2 O, K 2 O, Cs 2 O, MgO, CaO, SrO, BaO, ZnO, La 2 O 3 , Gd 2 O 3 , Y 2 O 3 , ZrO 2 , TiO 2 , Nb 2 O 5 , WO 3 and Bi 2 O 3 expressed in mass % are respectively C(SiO 2 ), C(B 2 O 3 ), C(Al 2 O 3 ), C(Li 2 O ), C(Na 2 O), C(K 2 O), C(Cs 2 O), C(MgO), C( CaO ), C(SrO), C(BaO), C(ZnO), C(La 2 O 3 ), C(Gd 2 O 3 ), and C(Cs 2 O ). O 3 ), C(Y 2 O 3 ), C(ZrO 2 ), C(TiO 2 ), C(Nb 2 O 5 ), C(WO 3 ) and C(Bi 2 O 3 ).
上述以外的玻璃成分Ta 2O 5、Sc 2O 3、HfO 2、Lu 2O 3、GeO 2及Yb 2O 3的以質量%表示的含量分別設為C(Ta 2O 5)、C(Sc 2O 3)、C(HfO 2)、C(Lu 2O 3)、C(GeO 2)及C(Yb 2O 3)。 The contents of the glass components Ta2O5 , Sc2O3 , HfO2 , Lu2O3 , GeO2 and Yb2O3 other than the above are expressed in mass % as C( Ta2O5 ) , C( Sc2O3 ) , C( HfO2 ), C( Lu2O3 ), C( GeO2 ) and C( Yb2O3 ) , respectively .
在第4實施方式中，將SiO 2、BO 1.5、AlO 1.5、LiO 0.5、NaO 0.5、KO 0.5、CsO 0.5、MgO、CaO、SrO、BaO、ZnO、LaO 1.5、GdO 1.5、YO 1.5、ZrO 2、TiO 2、NbO 2.5、WO 3及BiO 1.5的各化學式量分別設為M(SiO 2)、M(BO 1.5)、M(AlO 1.5)、M(LiO 0.5)、M(NaO 0.5)、M(KO 0.5)、M(CsO 0.5)、M(MgO)、M(CaO)、M(SrO)、M(BaO)、M(ZnO)、M(LaO 1.5)、M(GdO 1.5)、M(YO 1.5)、M(ZrO 2)、M(TiO 2)、M(NbO 2.5)、M(WO 3)及M(BiO 1.5)。 In the fourth embodiment, the chemical formula weights of SiO 2 , BO 1.5 , AlO 1.5 , LiO 0.5 , NaO 0.5 , KO 0.5 , CsO 0.5 , MgO, CaO, SrO, BaO, ZnO, LaO 1.5 , GdO 1.5 , YO 1.5 , ZrO 2 , TiO 2 , NbO 2.5 , WO 3 and BiO 1.5 are respectively M(SiO 2 ), M(BO 1.5 ), M(AlO 1.5 ), M(LiO 0.5 ), M(NaO 0.5 ), M(KO 0.5 ), M(CsO 0.5 ), M(MgO), M(CaO), M(SrO), M(BaO), M(ZnO), M(LaO 3) and BiO 1.5. 1.5 ), M(GdO 1.5 ), M(YO 1.5 ), M(ZrO 2 ), M(TiO 2 ), M(NbO 2.5 ), M(WO 3 ) and M(BiO 1.5 ).
上述以外的玻璃成分TaO 2.5、ScO 1.5、HfO 2、LuO 1.5、GeO 2及YbO 1.5的各化學式量分別設為M(TaO 2.5)、M(ScO 1.5)、M(HfO 2)、M(LuO 1.5)、M(GeO 2)及M(YbO 1.5)。 The chemical formulae of the glass components TaO 2.5 , ScO 1.5 , HfO 2 , LuO 1.5 , GeO 2 , and YbO 1.5 other than the above are M(TaO 2.5 ), M(ScO 1.5 ), M(HfO 2 ), M(LuO 1.5 ), M(GeO 2 ), and M(YbO 1.5 ), respectively.
即，在第4實施方式中，例如，關於氧化物X yO z，可以將以質量%表示的含量設為C(X yO z)。另外，可以將氧化物X yO z中的平均每1莫耳陽離子(陽離子「X」)的化學式量、即XO z/y中的化學式量設為M(XO z/y)。而且，以式{C(X yO z)/M(XO z/y)}表示的是以莫耳%表示的陽離子「X」的含量、即以陽離子%表示的「X」的含量。 That is, in the fourth embodiment, for example, regarding the oxide XyOz , the content expressed in mass% can be set to C( XyOz ). In addition, the chemical formula weight per 1 mol of cations (cation "X " ) in the oxide XyOz , that is, the chemical formula weight in XOz /y can be set to M( XOz/y ). Moreover, the content of cations " X " expressed in mole%, that is, the content of "X" expressed in cation % is expressed by the formula {C( XyOz )/M(XOz /y )}.
在第4實施方式的光學玻璃中，設定A1＝{C(B 2O 3)/M(BO 1.5)}/{C(B 2O 3)/M(BO 1.5)+C(SiO 2)/M(SiO 2)}時，A1為1/3以上。A1的下限較佳為1.1/3，進一步以1.2/3、1.3/3、1.4/3、1.5/3、1.6/3、1.7/3、1.8/3、1.9/3的順序更佳。另外，A1的上限較佳為3.0/3，進一步以2.9/3、2.8/3、2.7/3、2.6/3、2.5/3、2.4/3、2.3/3的順序更佳。 In the optical glass of the fourth embodiment, when A1={C(B 2 O 3 )/M(BO 1.5 )}/{C(B 2 O 3 )/M(BO 1.5 )+C(SiO 2 )/M(SiO 2 )}, A1 is 1/3 or more. The lower limit of A1 is preferably 1.1/3, and more preferably in the order of 1.2/3, 1.3/3, 1.4/3, 1.5/3, 1.6/3, 1.7/3, 1.8/3, and 1.9/3. The upper limit of A1 is preferably 3.0/3, and more preferably in the order of 2.9/3, 2.8/3, 2.7/3, 2.6/3, 2.5/3, 2.4/3, and 2.3/3.
藉由將A1設為上述範圍，能夠得到在-30~70℃下的平均線膨脹係數α L大的低色散的光學玻璃。另外，能夠降低玻璃的相對折射率的溫度係數(dn/dT)。即使在大量含有La 2O 3的情況下，也能夠抑制玻璃的熱穩定性的降低。另一方面，A1過小時，在大量包含作為提高折射率nd、防止平均線膨脹係數α L的降低的玻璃成分的La 2O 3及Y 2O 3的情況下，存在玻璃變得不穩定之虞。另外，A1過大時，存在玻璃的穩定性、化學耐久性及機械特性降低之虞。 By setting A1 to the above range, a low-dispersion optical glass having a large average linear expansion coefficient α L at -30 to 70°C can be obtained. In addition, the temperature coefficient of the relative refractive index of the glass (dn/dT) can be reduced. Even when a large amount of La 2 O 3 is contained, a decrease in the thermal stability of the glass can be suppressed. On the other hand, when A1 is too small, when a large amount of La 2 O 3 and Y 2 O 3 are contained as glass components for increasing the refractive index nd and preventing a decrease in the average linear expansion coefficient α L, there is a risk that the glass will become unstable. In addition, when A1 is too large, there is a risk that the stability, chemical durability and mechanical properties of the glass will be reduced.
在第4實施方式的光學玻璃中，設定B1＝{C(BaO)/M(BaO)+C(SrO)/M(SrO)}/{C(Li 2O)/M(LiO 0.5)+C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(Cs 2O)/M(CsO 0.5)+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}時，B1為0.62以上。B1的下限較佳為0.63，進一步以0.65、0.67、0.69、0.71、0.73、0.75、0.77、0.79、0.81、0.83、0.85、0.87的順序更佳。另外，B1的上限較佳為1.00，進一步以0.99、0.98的順序更佳。B1也可以為1.00。 In the optical glass of the fourth embodiment, when B1={C(BaO)/M(BaO)+C(SrO)/M(SrO)}/{C( Li2O )/M( LiO0.5 )+C( Na2O )/M( NaO0.5 )+C( K2O )/M( KO0.5 )+C( Cs2O )/M( CsO0.5 )+C(MgO)/M(MgO)+C(CaO)/M(CaO)+C(SrO)/M(SrO)+C(BaO)/M(BaO)}, B1 is 0.62 or more. The lower limit of B1 is preferably 0.63, and more preferably in the order of 0.65, 0.67, 0.69, 0.71, 0.73, 0.75, 0.77, 0.79, 0.81, 0.83, 0.85, and 0.87. In addition, the upper limit of B1 is preferably 1.00, and more preferably in the order of 0.99 and 0.98. B1 may also be 1.00.
藉由將B1設為上述範圍，可得到平均線膨脹係數α L大的高折射率的光學玻璃。另外，能夠增大平均線膨脹係數α L，並且抑制熱穩定性的降低。另一方面，B1過小時，存在平均線膨脹係數α L及折射率nd降低、玻璃的穩定性受損之虞。 By setting B1 to the above range, an optical glass having a large average linear expansion coefficient α L and a high refractive index can be obtained. In addition, the average linear expansion coefficient α L can be increased and the decrease in thermal stability can be suppressed. On the other hand, when B1 is too small, there is a possibility that the average linear expansion coefficient α L and the refractive index nd decrease, and the stability of the glass may be impaired.
在第4實施方式的光學玻璃中，設定C1＝{C(BaO)/M(BaO)+C(Li 2O)/M(LiO 0.5)}/{C(Na 2O)/M(NaO 0.5)+C(K 2O)/M(KO 0.5)+C(SiO 2)/M(SiO 2)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)}時，C1為8/9以上。C1的下限較佳為8.2/9，進一步以8.4/9、8.6/9、8.8/9、9.0/9、9.2/9、9.4/9、9.5/9的順序更佳。另外，C1的上限較佳為27/9，進一步以25/9、23/9、21/9、19/9、17/9、15/9、13/9、12/9的順序更佳。 In the optical glass of the fourth embodiment, when C1={C(BaO)/M(BaO)+C(Li 2 O)/M(LiO 0.5 )}/{C(Na 2 O)/M(NaO 0.5 )+C(K 2 O)/M(KO 0.5 )+C(SiO 2 )/M(SiO 2 )+C(TiO 2 )/M(TiO 2 )+C(Nb 2 O 5 )/M(NbO 2.5 )+C(WO 3 )/M(WO 3 )}, C1 is 8/9 or more. The lower limit of C1 is preferably 8.2/9, more preferably in the order of 8.4/9, 8.6/9, 8.8/9, 9.0/9, 9.2/9, 9.4/9, and 9.5/9. In addition, the upper limit of C1 is preferably 27/9, and further preferably in the order of 25/9, 23/9, 21/9, 19/9, 17/9, 15/9, 13/9, and 12/9.
藉由將C1設為上述範圍，可得到平均線膨脹係數α L大的高折射率低色散性的光學玻璃。另外，能夠降低玻璃的相對折射率的溫度係數(dn/dT)。另一方面，C1過小時，存在平均線膨脹係數α L降低、玻璃的高折射低色散性喪失之虞。另外，C1過大時，存在玻璃的穩定性降低之虞。 By setting C1 to the above range, an optical glass with a high refractive index and low dispersion having a large average linear expansion coefficient α L can be obtained. In addition, the temperature coefficient (dn/dT) of the relative refractive index of the glass can be reduced. On the other hand, when C1 is too small, there is a risk that the average linear expansion coefficient α L is reduced and the high refractive index and low dispersion of the glass are lost. In addition, when C1 is too large, there is a risk that the stability of the glass is reduced.
在第4實施方式的光學玻璃中，設為D1＝C(Gd 2O 3)+C(ZnO)+C(TiO 2)+C(Nb 2O 5)+C(WO 3)+C(ZrO 2)時，D1為13.50以下。D1的上限較佳為12.00，進一步以11.00、10.50、10.00、9.50、9.00、8.50的順序更佳。另外，D1的下限較佳為0，進一步以1、2、3、4、5、6、7、8的順序更佳。D1也可以為0。 In the optical glass of the fourth embodiment, when D1=C( Gd2O3 ) +C(ZnO)+C( TiO2 )+C( Nb2O5 )+C( WO3 )+C( ZrO2 ), D1 is 13.50 or less. The upper limit of D1 is preferably 12.00, more preferably in the order of 11.00, 10.50, 10.00, 9.50, 9.00, and 8.50. The lower limit of D1 is preferably 0, more preferably in the order of 1, 2 , 3, 4, 5, 6, 7, and 8. D1 may be 0.
藉由將D1設為上述範圍，能夠抑制平均線膨脹係數α L的降低。另外，可抑制高色散化，得到高折射率低色散性的光學玻璃。此外，還具有不增大玻璃的相對折射率的溫度係數(dn/dT)的效果。D1可以為0，但為了調整阿貝數νd等光學常數，也可以將D1設為大於0。另一方面，D1過大時，存在平均線膨脹係數α L降低、並且玻璃的高折射低色散性損失之虞。 By setting D1 to the above range, the decrease in the average linear expansion coefficient α L can be suppressed. In addition, high dispersion can be suppressed to obtain an optical glass with a high refractive index and low dispersion. In addition, it also has the effect of not increasing the temperature coefficient (dn/dT) of the relative refractive index of the glass. D1 can be 0, but in order to adjust optical constants such as the Abbe number νd, D1 can also be set to be greater than 0. On the other hand, when D1 is too large, there is a risk that the average linear expansion coefficient α L is reduced and the high refractive index and low dispersion of the glass are lost.
在第4實施方式的光學玻璃中，設定E1＝{C(La 2O 3)+C(Gd 2O 3)+C(Y 2O 3)}/{C(SiO 2)+C(B 2O 3)+C(Al 2O 3)}時，E1為1.25以上。E1的下限較佳為1.30，進一步以1.35、1.40、1.45、1.50、1.55、1.60、1.65、1.70的順序更佳。另外，E1的上限較佳為3.00，進一步以2.80、2.60、2.40、2.20、2.10的順序更佳。 In the optical glass of the fourth embodiment, when E1={C(La 2 O 3 )+C(Gd 2 O 3 )+C(Y 2 O 3 )}/{C(SiO 2 )+C(B 2 O 3 )+C(Al 2 O 3 )}, E1 is 1.25 or more. The lower limit of E1 is preferably 1.30, more preferably in the order of 1.35, 1.40, 1.45, 1.50, 1.55, 1.60, 1.65, and 1.70. The upper limit of E1 is preferably 3.00, more preferably in the order of 2.80, 2.60, 2.40, 2.20, and 2.10.
藉由將E1設為上述範圍，可得到高折射率低色散性的光學玻璃。另一方面，E1過小時，存在玻璃的高折射高色散性損失、平均線膨脹係數α L降低之虞。另外，E1過大時，存在玻璃的熱穩定性降低之虞。 By setting E1 to the above range, an optical glass with high refractive index and low dispersion can be obtained. On the other hand, when E1 is too small, there is a risk that the high refractive index and high dispersion of the glass will be lost and the average linear expansion coefficient α L will decrease. In addition, when E1 is too large, there is a risk that the thermal stability of the glass will decrease.
在第4實施方式的光學玻璃中，設定G1＝C(BaO)/M(BaO)+C(La 2O 3)/M(LaO 1.5)+C(Li 2O)/M(LiO 0.5)+C(Y 2O 3)/M(YO 1.5)時，G1為0.47以上。G1的下限較佳為0.475，進一步以0.48、0.485的順序更佳。另外，G1的上限較佳為0.60，進一步以0.59、0.58、0.57、0.56、0.55、0.54、0.53的順序更佳。 In the optical glass of the fourth embodiment, when G1=C(BaO)/M(BaO)+C(La 2 O 3 )/M(LaO 1.5 )+C(Li 2 O)/M(LiO 0.5 )+C(Y 2 O 3 )/M(YO 1.5 ), G1 is 0.47 or more. The lower limit of G1 is preferably 0.475, more preferably in the order of 0.48 and 0.485. The upper limit of G1 is preferably 0.60, more preferably in the order of 0.59, 0.58, 0.57, 0.56, 0.55, 0.54 and 0.53.
藉由將G1設為上述範圍，可以得到能夠抑制平均線膨脹係數α L的降低、並且高折射率低色散性的光學玻璃。另一方面，G1過小時，存在平均線膨脹係數α L降低、玻璃的高折射低色散性喪失之虞。另外，G1過大時，存在玻璃的熱穩定性降低之虞。 By setting G1 to the above range, it is possible to obtain an optical glass with high refractive index and low dispersion while suppressing the decrease in the average linear expansion coefficient α L. On the other hand, when G1 is too small, there is a risk that the average linear expansion coefficient α L decreases and the high refractive index and low dispersion of the glass are lost. In addition, when G1 is too large, there is a risk that the thermal stability of the glass decreases.
在第4實施方式的光學玻璃中，設定F1＝{C(Gd 2O 3)/M(GdO 1.5)+C(ZnO)/M(ZnO)+C(TiO 2)/M(TiO 2)+C(Nb 2O 5)/M(NbO 2.5)+C(WO 3)/M(WO 3)+C(Bi 2O 3)/M(BiO 1.5)}/{C(Y 2O 3)/M(YO 1.5)}時，F1的上限較佳為2.0，進一步以1.8、1.6、1.4、1.2、1.1、1.0、0.9、0.8、0.6的順序更佳。另外，F1的下限較佳為0，進一步以0.1、0.2、0.3、0.4的順序更佳。F1可以為0。 In the optical glass of the fourth embodiment, when F1={C( Gd2O3 )/M( GdO1.5 )+C ( ZnO )/M(ZnO)+C( TiO2 )/M(TiO2)+C( Nb2O5 )/M( NbO2.5 )+C( WO3 )/M( WO3 )+C(Bi2O3)/M( BiO1.5 )}/{C( Y2O3 )/M( YO1.5 )}, the upper limit of F1 is preferably 2.0, and more preferably in the order of 1.8 , 1.6 , 1.4, 1.2, 1.1, 1.0 , 0.9 , 0.8, and 0.6. In addition, the lower limit of F1 is preferably 0, and more preferably in the order of 0.1, 0.2, 0.3, and 0.4. F1 can be 0.
從提高平均線膨脹係數α L、抑制玻璃的熱穩定性的降低的觀點考慮，F1較佳設為上述範圍。F1可以為0，但為了調整阿貝數νd等光學常數，也可以將F1設為大於0。另一方面，F1過大時，存在平均線膨脹係數α L降低、並且玻璃的高折射低色散性喪失之虞。 From the viewpoint of increasing the average linear expansion coefficient α L and suppressing the decrease in the thermal stability of the glass, F1 is preferably set to the above range. F1 can be 0, but in order to adjust optical constants such as the Abbe number νd, F1 can also be set to be greater than 0. On the other hand, when F1 is too large, there is a risk that the average linear expansion coefficient α L decreases and the high refractive index and low dispersion of the glass are lost.
在第4實施方式的光學玻璃中，上述以外的玻璃成分的含量及比率可以設為與第3實施方式同樣。In the optical glass of the fourth embodiment, the contents and ratios of the glass components other than those described above can be the same as those of the third embodiment.
在第4實施方式的光學玻璃中，可以將玻璃特性設為與第1實施方式同樣。In the optical glass of the fourth embodiment, the glass properties can be set to be the same as those of the first embodiment.
可以將第4實施方式的光學玻璃的製造及光學元件等的製造設為與第1實施方式同樣。The production of the optical glass and the production of the optical elements, etc., of the fourth embodiment can be made the same as those of the first embodiment.
以下，藉由實施例對本發明進行說明，但本發明不僅限定於以下的實施例。Hereinafter, the present invention will be described by way of examples, but the present invention is not limited to the following examples.
(實施例1) 在實施例1中，表1(2-1)~(2-3)、(3-1)~(3-3)及(4-1)~(4-3)中示出的數值是根據表1(1-1)~(1-3)中所示的玻璃組成計算出的值。同樣，表2(2-1)~(2-3)、(3-1)~(3-3)及(4-1)~(4-3)中示出的數值是根據表2(1-1)~(1-3)中所示的玻璃組成計算出的值。 (Example 1) In Example 1, the values shown in Table 1 (2-1) to (2-3), (3-1) to (3-3) and (4-1) to (4-3) are values calculated based on the glass composition shown in Table 1 (1-1) to (1-3). Similarly, the values shown in Table 2 (2-1) to (2-3), (3-1) to (3-3) and (4-1) to (4-3) are values calculated based on the glass composition shown in Table 2 (1-1) to (1-3).
在實施例1中，在表1(1-1)~(1-3)中以陽離子%表示，在表2(1-1)~(1-3)中以質量%表示，示出試樣No.1~122及比較例A的玻璃組成。即，在表1(1-1)~(1-3)和表2(1-1)~(1-3)中，玻璃組成的表示方法不同，但相同試樣No.的光學玻璃是指具有相同組成的相同光學玻璃。因此，表1(1-1)~(1-3)及表2(1-1)~(1-3)示出實質上相同的光學玻璃及其結果。In Example 1, the glass compositions of Samples No. 1 to 122 and Comparative Example A are shown in terms of cation % in Table 1 (1-1) to (1-3) and in terms of mass % in Table 2 (1-1) to (1-3). That is, in Table 1 (1-1) to (1-3) and Table 2 (1-1) to (1-3), the methods of expressing the glass compositions are different, but the optical glasses of the same Sample No. refer to the same optical glasses having the same composition. Therefore, Table 1 (1-1) to (1-3) and Table 2 (1-1) to (1-3) show substantially the same optical glasses and their results.
需要說明的是，關於表1(1-1)~(1-3)，藉由陽離子%表示玻璃組成，陰離子成分的總量均為O 2-。即，表1(1-1)~(1-3)中記載的組成中的O 2-的含量均為100陰離子%。 It should be noted that, in Table 1 (1-1) to (1-3), the glass composition is expressed by cation %, and the total amount of anion components is O 2- . That is, the content of O 2- in the composition recorded in Table 1 (1-1) to (1-3) is 100 anion %.
另外，將表2(1-1)~(1-3)中的質量%表示的組成轉換成表1(1-1)~(1-3)中的陽離子%表示的組成。In addition, the compositions expressed in mass % in Table 2 (1-1) to (1-3) were converted into compositions expressed in cation % in Table 1 (1-1) to (1-3).
[玻璃樣品的製作] 以成為具有表1(1-1)~(1-3)、表2(1-1)~(1-3)中示出的試樣No.1~122及比較例A的組成的玻璃的方式，稱量與各成分對應的化合物原料、即磷酸鹽、碳酸鹽、氧化物等原料，充分混合，製成調配原料。以得到150g的玻璃的方式對該調配原料進行調配。將該調配原料投入鉑製坩堝，在大氣環境中加熱至1200~1400℃，進行熔融，藉由攪拌進行均勻化、澄清，得到了熔融玻璃。將該熔融玻璃注入成型模具而進行成型，緩慢冷卻，得到了塊狀的玻璃樣品。 需要說明的是，也可以將調配原料投入石英玻璃製坩堝，熔融後，移動至鉑製坩堝，進一步進行加熱、熔融，藉由攪拌進行均勻化、澄清，將所得到的熔融玻璃注入成型模具而進行成型，緩慢冷卻。 [Preparation of glass samples] In order to obtain glass having the composition of Sample No. 1 to 122 and Comparative Example A shown in Table 1 (1-1) to (1-3), Table 2 (1-1) to (1-3), the compound raw materials corresponding to each component, i.e., phosphate, carbonate, oxide and other raw materials, are weighed and fully mixed to prepare the prepared raw materials. The prepared raw materials are prepared in such a way that 150 g of glass is obtained. The prepared raw materials are placed in a platinum crucible, heated to 1200 to 1400°C in an atmospheric environment, melted, and homogenized and clarified by stirring to obtain molten glass. The molten glass is injected into a molding mold to be molded, and slowly cooled to obtain a block-shaped glass sample. It should be noted that the prepared raw materials can also be put into a quartz glass crucible, melted, and then moved to a platinum crucible for further heating and melting, and then homogenized and clarified by stirring. The resulting molten glass can be injected into a molding mold for molding and slowly cooled.
[玻璃樣品的評價] 對於所得到的玻璃樣品，再次進行加熱，在退火溫度I(℃)下保持0.5hr後，以降溫速度-30℃/hr緩慢冷卻至比退火溫度I低120℃的溫度。退火溫度I為比玻璃化轉變溫度Tg高8℃的溫度(Tg+8℃)以上，設定為比Tg高27℃的溫度(Tg+27℃)以下。 [Evaluation of glass samples] The obtained glass samples were heated again, kept at annealing temperature I (℃) for 0.5 hr, and then slowly cooled at a cooling rate of -30℃/hr to a temperature 120℃ lower than annealing temperature I. Annealing temperature I is set to a temperature 8℃ higher than glass transition temperature Tg (Tg+8℃) or higher, and set to a temperature 27℃ higher than Tg (Tg+27℃) or lower.
如上所述，對於再次進行加熱而進行了退火的玻璃樣品，藉由以下示出的方法對玻璃組成、折射率nd、阿貝數νd、玻璃化轉變溫度Tg、比重、λ80、λ70、λ5、平均線膨脹係數α L、平均線膨脹係數α 100-300進行了測定，將結果示於表3。 As described above, for the glass sample that was heated again and annealed, the glass composition, refractive index nd, Abbe number νd, glass transition temperature Tg, specific gravity, λ80, λ70, λ5, average linear expansion coefficient α L , and average linear expansion coefficient α 100-300 were measured by the method shown below. The results are shown in Table 3.
〔1〕玻璃組成 對於所得到的玻璃樣品，藉由電感耦合電漿原子發射光譜法(ICP-AES)對各玻璃成分的含量進行了測定。需要說明的是，在表1中示出的試樣No.1~122及比較例A的全部玻璃樣品中，F的含量為0%。 [1] Glass composition The content of each glass component of the obtained glass samples was measured by inductively coupled plasma atomic emission spectroscopy (ICP-AES). It should be noted that the content of F in all glass samples of Sample No. 1 to 122 and Comparative Example A shown in Table 1 was 0%.
〔2〕比重 基於日本光學玻璃工業協會標準JOGIS05進行了測定。 [2] Specific gravity Measured based on the Japan Optical Glass Industries Association standard JOGIS05.
〔3〕折射率nd及阿貝數νd 基於日本工業標準JISB-7071-1進行了測定。 [3] Refractive index nd and Abbe number νd Measured based on Japanese Industrial Standard JIS B-7071-1.
〔4〕λ80、λ70、λ5 將玻璃樣品加工成厚度10mm、具有相互平行且經過了光學拋光的平面，對波長280nm~700nm的波長範圍中的分光透射率進行了測定。將垂直入射至經過了光學拋光的一個平面的光線的強度設為強度A，將從另一個平面出射的光線的強度設為強度B，計算出分光透射率B/A。將分光透射率達到80%的波長設為λ80，將分光透射率達到70%的波長設為λ70，將分光透射率達到5%的波長設為λ5。需要說明的是，分光透射率中包含試樣表面的光線的反射損失。 〔4〕λ80, λ70, λ5 Glass samples were processed into 10mm thick, parallel and optically polished planes, and the spectral transmittance in the wavelength range of 280nm~700nm was measured. The intensity of light perpendicularly incident on one optically polished plane was set as intensity A, and the intensity of light emitted from the other plane was set as intensity B, and the spectral transmittance B/A was calculated. The wavelength at which the spectral transmittance reached 80% was set as λ80, the wavelength at which the spectral transmittance reached 70% was set as λ70, and the wavelength at which the spectral transmittance reached 5% was set as λ5. It should be noted that the spectral transmittance includes the reflection loss of light on the sample surface.
〔5〕玻璃化轉變溫度Tg 使用熱機械分析裝置(TMA)(MAC Science制、TMA-4000S)，以升溫速度4℃/分對玻璃化轉變溫度Tg進行了測定。 [5] Glass transition temperature Tg The glass transition temperature Tg was measured using a thermomechanical analyzer (TMA) (manufactured by MAC Science, TMA-4000S) at a heating rate of 4°C/min.
〔6〕平均線膨脹係數α L對於所得到的玻璃樣品，參照JOGIS16的規定對平均線膨脹係數進行了測定。使用NETZSCH JAPAN公司製造的熱機械分析裝置(TMA4000SE)對平均線膨脹係數進行了測定。試樣設為長度20mm±0.5mm、直徑5mm±0.5mm的圓棒。首先，使用液態氮將試樣溫度冷卻至-80℃以下，保持20分鐘後，開始測定。測定中，在對試樣施加了98mN的負載的狀態下，一邊以每分鐘4℃的恆定速度升溫至320℃，一邊以1秒鐘的間隔測定溫度和試樣的伸長率。將在-30~70℃下的線膨脹係數的平均值作為平均線膨脹係數α L。 [6] Average linear expansion coefficient α L For the obtained glass sample, the average linear expansion coefficient was measured with reference to the provisions of JOGIS16. The average linear expansion coefficient was measured using a thermomechanical analyzer (TMA4000SE) manufactured by NETZSCH JAPAN. The sample was set as a round rod with a length of 20 mm ± 0.5 mm and a diameter of 5 mm ± 0.5 mm. First, the sample temperature was cooled to below -80°C using liquid nitrogen, and after maintaining it for 20 minutes, the measurement was started. During the measurement, a load of 98 mN was applied to the sample, while the temperature was raised to 320°C at a constant rate of 4°C per minute, and the temperature and the elongation of the sample were measured at intervals of 1 second. The average value of the linear expansion coefficient at -30 to 70°C is taken as the average linear expansion coefficient α L .
〔7〕平均線膨脹係數α 100-300對於所得到的玻璃樣品，參照JOGIS08的規定，對平均線膨脹係數進行了測定。使用NETZSCH JAPAN公司製造的熱機械分析裝置(TMA4000SE)對平均線膨脹係數進行了測定。試樣設為長度20mm±0.5mm、直徑5mm±0.5mm的圓棒。測定中，在對試樣施加了98mN的負載的狀態下，一邊以每分鐘4℃的一定速度進行升溫，一邊以1秒鐘的間隔測定溫度和試樣的伸長率。將在100~300℃下的線膨脹係數的平均值作為平均線膨脹係數α 100-300。 [7] Average linear expansion coefficient α 100-300 For the obtained glass samples, the average linear expansion coefficient was measured with reference to the provisions of JOGIS08. The average linear expansion coefficient was measured using a thermomechanical analyzer (TMA4000SE) manufactured by NETZSCH JAPAN. The sample was set as a round rod with a length of 20mm±0.5mm and a diameter of 5mm±0.5mm. During the measurement, a load of 98mN was applied to the sample, while the temperature was increased at a constant rate of 4°C per minute, and the temperature and the elongation of the sample were measured at intervals of 1 second. The average value of the linear expansion coefficient at 100~300°C was taken as the average linear expansion coefficient α 100-300 .
(實施例2) 對於實施例1中得到的玻璃樣品中的No.20及具有比較例A的組成的樣品，藉由以下示出的方法，對相對折射率的溫度係數(dn/dT)進行了測定，將結果示於表4。 (Example 2) For glass sample No. 20 obtained in Example 1 and the sample having the composition of Comparative Example A, the temperature coefficient of relative refractive index (dn/dT) was measured by the method shown below, and the results are shown in Table 4.
〔8〕相對折射率的溫度係數dn/dT 對於所得到的玻璃樣品，再次進行加熱，以退火溫度II(℃)保持了12hr後，以降溫速度-10℃/hr緩慢冷卻至比退火溫度II低200℃的溫度。退火溫度II如下所述地進行設定。 ・玻璃化轉變溫度Tg(℃)的個位為0~2的情況：用將Tg的個位設為0的值減去10，將所得到的溫度作為退火溫度II。 ・玻璃化轉變溫度Tg(℃)的個位為3~9的情況：將Tg的個位設為0，將所得到的值作為退火溫度II。 [8] Temperature coefficient of relative refractive index dn/dT The obtained glass sample was heated again, kept at annealing temperature II (℃) for 12 hours, and then slowly cooled at a cooling rate of -10℃/hr to a temperature 200℃ lower than annealing temperature II. Annealing temperature II was set as follows. ・When the unit digit of the glass transition temperature Tg (℃) is 0 to 2: subtract 10 from the value with the unit digit of Tg set to 0, and the resulting temperature is annealing temperature II. ・When the unit digit of the glass transition temperature Tg (℃) is 3 to 9: set the unit digit of Tg to 0, and the resulting value is annealing temperature II.
如上所述，對於再次進行加熱並進行了退火的玻璃樣品，藉由日本工業標準JISB7072-2(光學玻璃中的折射率的溫度係數的測定方法-第2部：干涉法)，對於波長632.8nm的光測定使溫度從-40℃變化至110℃時的相對折射率的溫度係數的值。其中，在實施例中，示出了使溫度從20℃變化至40℃時的相對折射率的溫度係數：dn/dT(rel.＠632.8、20-40℃)的值作為代表。另外，作為相對折射率的溫度係數的溫度依賴性的指標，求出將使溫度從-40℃變化至80℃時的dn/dT＠632.8相對於溫度的變化代入線性近似式(y＝ax+b)時的斜率a。另外，求出截距b、也就是上述近似式中的0℃下的dn/dT＠632.8的值。具體而言，在-30℃至70℃的範圍中，將間隔20℃的6個點的值代入線性近似式，求出各斜率a及截距b。As described above, for the glass sample that was heated again and annealed, the temperature coefficient of the relative refractive index when the temperature was changed from -40°C to 110°C was measured for light with a wavelength of 632.8nm according to Japanese Industrial Standard JIS B7072-2 (Determination method of temperature coefficient of refractive index in optical glass - Part 2: Interference method). In the embodiment, the value of the temperature coefficient of the relative refractive index when the temperature was changed from 20°C to 40°C: dn/dT (rel.@632.8, 20-40°C) is shown as a representative. In addition, as an index of the temperature dependence of the temperature coefficient of relative refractive index, the slope a is obtained when the change of dn/dT@632.8 with respect to the temperature when the temperature is changed from -40°C to 80°C is substituted into the linear approximation formula (y=ax+b). In addition, the intercept b, that is, the value of dn/dT@632.8 at 0°C in the above approximation formula is obtained. Specifically, in the range of -30°C to 70°C, the values of 6 points at intervals of 20°C are substituted into the linear approximation formula, and the slope a and intercept b are obtained.
(實施例3) 對實施例1中得到的玻璃樣品進行切割、磨削，製作了碎片。藉由再熱壓對碎片進行壓製成型，製作了光學元件毛坯。對光學元件毛坯進行精密退火，以成為所需的折射率的方式精密地調整了折射率後，藉由已知的方法進行磨削、拋光，由此得到了雙凸透鏡、雙凹透鏡、平凸透鏡、平凹透鏡、凹彎月透鏡、凸彎月透鏡等各種透鏡。 (Example 3) The glass sample obtained in Example 1 was cut and ground to produce fragments. The fragments were pressed and molded by hot pressing to produce optical element blanks. The optical element blanks were precisely annealed, and the refractive index was precisely adjusted to the desired refractive index. Then, they were ground and polished by known methods to obtain various lenses such as biconvex lenses, biconcave lenses, plano-convex lenses, plano-concave lenses, concave meniscus lenses, and convex meniscus lenses.
應該理解的是，本次公開的實施方式全部是示例性的，並不構成限制。本發明的範圍由申請專利範圍、而不是上述的說明界定，旨在包括與請求項等同的含義及範圍內的全部變形。It should be understood that the embodiments disclosed herein are all exemplary and do not constitute limitations. The scope of the invention is defined by the scope of the patent application, not the above description, and is intended to include all variations within the meaning and scope equivalent to the claims.
例如，對於上述示例的玻璃組成，藉由說明書中記載的組成調整，可以製作本發明的一個方式的光學玻璃。 另外，當然可以將說明書中示例出的或作為較佳的範圍記載的事項中的2個以上任意組合。 For example, for the glass composition exemplified above, by adjusting the composition described in the specification, an optical glass of one embodiment of the present invention can be produced. In addition, of course, any combination of two or more of the items exemplified in the specification or described as a preferred range can be used.
無。without.
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Claims (6)
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|---|---|---|---|
| JP2023-014178 | 2023-02-01 | ||
| JP2023014178A JP2024109404A (en) | 2023-02-01 | 2023-02-01 | Optical glass and optical element |
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| TWI860239B true TWI860239B (en) | 2024-10-21 |
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| JP (1) | JP2024109404A (en) |
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|---|---|---|---|---|
| TW202241824A (en) * | 2021-03-31 | 2022-11-01 | 日商Ｈｏｙａ股份有限公司 | Optical glass and optical element having a small Abbe number vd and a high relative partial dispersion PC, t in the infrared wavelength region |
| TW202246191A (en) * | 2021-05-21 | 2022-12-01 | 日商Ｈｏｙａ股份有限公司 | Optical glass and optical element having a small Abbe number and a high relative partial dispersion in an infrared wavelength region |
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2023
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| TW202241824A (en) * | 2021-03-31 | 2022-11-01 | 日商Ｈｏｙａ股份有限公司 | Optical glass and optical element having a small Abbe number vd and a high relative partial dispersion PC, t in the infrared wavelength region |
| TW202246191A (en) * | 2021-05-21 | 2022-12-01 | 日商Ｈｏｙａ股份有限公司 | Optical glass and optical element having a small Abbe number and a high relative partial dispersion in an infrared wavelength region |
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| TW202432485A (en) | 2024-08-16 |
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