CN1562838A - Laser glass of germanate possessing upper transition luminescence - Google Patents

Laser glass of germanate possessing upper transition luminescence Download PDF

Info

Publication number
CN1562838A
CN1562838A CN 200410017066 CN200410017066A CN1562838A CN 1562838 A CN1562838 A CN 1562838A CN 200410017066 CN200410017066 CN 200410017066 CN 200410017066 A CN200410017066 A CN 200410017066A CN 1562838 A CN1562838 A CN 1562838A
Authority
CN
China
Prior art keywords
glass
sample
10bao
10zno
germanate
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
CN 200410017066
Other languages
Chinese (zh)
Inventor
杨中民
姜中宏
杨建虎
戴世勋
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Shanghai Institute of Optics and Fine Mechanics of CAS
Original Assignee
Shanghai Institute of Optics and Fine Mechanics of CAS
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Shanghai Institute of Optics and Fine Mechanics of CAS filed Critical Shanghai Institute of Optics and Fine Mechanics of CAS
Priority to CN 200410017066 priority Critical patent/CN1562838A/en
Publication of CN1562838A publication Critical patent/CN1562838A/en
Pending legal-status Critical Current

Links

Images

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
    • C03C4/00—Compositions for glass with special properties
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/12—Silica-free oxide glass compositions
    • C03C3/253—Silica-free oxide glass compositions containing germanium
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C4/00—Compositions for glass with special properties
    • C03C4/12—Compositions for glass with special properties for luminescent glass; for fluorescent glass

Abstract

The compounds of the glass are (mol%): GeO2 10 is less than or equal to GeO2 is less than or equal to 55; TeO2O less than TeO2 is less than or equal to 45; PbO+Bi2O3=20; BaO=10, ZnO=10; R2O (R=Li, Na, K)=5, La2O3O less than La2O3 is less than or equal to 2. Said glass has maximum phonon energy same as tellurate glass and green luminescence strength. In range from room temp. to glass melted, devitrificating state does not created.

Description

Germanate laser glass with up-conversion luminescence
Technical field
The present invention relates to laserable material, particularly a kind of germanate laser glass material with up-conversion luminescence.
Background technology
The value because the blue green light wave band of laser has a wide range of applications in fields such as high density data storage, submarine communication, large screen display (needing blue green light to construct panchromatic demonstration), detection and laser medicines.As in optical disc storage,, existing CD capacity can be improved about 4 times with the alternative ruddiness " read/write head " of short wavelength's blue-greenish colour laser; In Laser Printing equipment, blue-greenish colour laser can improve print speed and resolving power; In submarine communication, bluish-green laser becomes window of transmission under water or the like because of its splendid penetrativity to seawater.The laser apparatus of at present typical blue green light wave band is an Argon ion laser, and the wavelength of its output is 488.0nm and 514.5nm.Volume is big, the life-span short and the shortcoming of job insecurity and this gas laser exists.In addition, it is difficult to utilize laser modulation technique to obtain high peak power by continuous mode work.For solid statelaser, the method that obtains bluish-green laser output mainly contains following several: (1) utilizes semiconductor material with wide forbidden band directly to make the semiconductor laser of bluish-green wave band; (2) utilize the nonlinear frequency transformation technology that Solid State Laser is carried out frequency multiplication; (3) switch technology realizes bluish-green laser output in the utilization in the crystal of mixing rare earth or glass.For the semiconductor laser diode (hereinafter to be referred as LD) of visible waveband, there is certain difficulty in exploitation blue, green glow LD, and the beam quality of LD is unsatisfactory simultaneously, is restricted in many Application Areass; And, need complicated non-linear parameter process carry out frequency inverted by the frequency multiplication solid statelaser of LD pumping, and though beam quality is fine, system is complicated, cost is very high.Switch technology in the utilization can obtain bluish-green laser output with the rare-earth-ion-doped crystal of near infrared LD pumping, glass.Compare with rare-earth-ion-doped crystal, glass has significant advantage: (1) output wavelength is many.Utilize the abundant energy level of rare earth ion, mix the up-conversion lasing that different rare earth ions can obtain different wave length (from the near infrared to the UV-light).Even mix with a kind of rare earth ion (as Pr 3+), also can obtain Multi Colour Lasers.
(2) do not need strict phase matched, the Doped Rare Earth ion has formed the Stark division of rare earth ion energy level owing to the constraint that is subjected to the lattice electric field in host glass, simultaneously between these splitted levels because the generation of phonon causes energy exchange with burying in oblivion, thereby caused these energy levels evenly or inhomogeneous broadening.Thereby it is not high to the stability requirement of excitation wavelength;
(3) glass can be made different shape and size, be made into micro-slice laser, can also be drawn into optical fiber and make conversion optical fiber laser.
At present mostly the up-conversion luminescence substrate material that uses is fluoride glass, but shortcomings such as mechanical strength is low because fluoride glass has, chemical stability and poor heat stability make it run into very big difficulty when fibre-optical drawing.Oxide glass has then effectively overcome the deficiency of fluoride glass, has higher mechanical strength and excellent chemistry and thermostability.In oxide glass, tellurate glass becomes the comparatively ideal conversion substrate material of going up because of it has lower phonon energy.But tellurate glass has the relatively poor shortcoming of thermostability equally, in fiber draw process, be easy to generate the crystallization phenomenon (referring to U.S.Patent 6356387, date of publication is on March 12nd, 2002, name is called TELLURITE GLASS, OPTICAL AMPLIFIER, AND LIGHTSOURCE), this also makes it be difficult to realize the successful drawing of optical fiber.
Summary of the invention
The technical problem to be solved in the present invention is to provide a kind of germanate laser glass with up-conversion luminescence, and this material can overcome the shortcoming of tellurate glass poor heat stability effectively on the basis of keeping the better up-conversion luminescence character of tellurate glass.
Basic thought of the present invention is by selecting the suitable network ectosome, improve the formation ability of glass, and add germanium oxide in tellurate glass, making the interlacing network structure of the molten mutually formation of itself and tellurium oxide, to increase the thermostability of tellurate glass.
Concrete technical solution of the present invention is as follows:
A kind of germanate laser glass with up-conversion luminescence is characterized in that this glass comprises following composition:
Component composition range (mol%)
GeO 2 10≤GeO 2≤55
TeO 2 0＜TeO 2≤45
PbO+Bi 2O 3 PbO+Bi 2O 3＝20
BaO BaO＝10
ZnO ZnO＝10
R 2O(R＝Li，Na，K) R 2O＝5
Yb 3++Tm 3++Er 3+ 0＜Yb 3++Tm 3++Er 3+＜2
The germanate laser glass of up-conversion luminescence of the present invention has following characteristic:
(1) has thermostability preferably, to the temperature range of glass melting, do not occur the crystallization phenomenon in the glass, can satisfy the wire drawing requirement of glass in the wire-drawing temperature scope in room temperature;
(2) this kind glass has and tellurate glass (75TeO 2-20ZnO-5Na 2O, referring to U.S.Patent 710961, date of publication on November 14th, 2000, name is called Tellurite glass, opticalamplifier, and light source) close maximum phonon energy;
(3) this glass and existing tellurate glass (75TeO 2-20ZnO-5Na 2O) compare, have suitable green luminescence intensity.
Description of drawings
Fig. 1 is tellurate glass (75TeO 2-20ZnO-5Na 2O) differential thermal analysis curve.
Fig. 2 is that the present invention has different tellurium ge content DTA on Glass curves.
Fig. 3 has the glass differential thermal analysis curve of different plumbous bi contents for the present invention.
Fig. 4 is different alkali-metal glass differential thermal analysis curves for the present invention contains.
Fig. 5 contains the glass differential thermal analysis curve of different rare earth ions for the present invention.
Fig. 6 is glass (55GeO of the present invention 2-20PbO-10BaO-10ZnO-5K 2O-1.0Yb 2O 3-0.2Er 2O 3, 45TeO 2-20GeO 2-20PbO-10BaO-10ZnO-5K 2O-1.0Yb 2O 3-0.2Er 2O 3) and tellurate glass (75TeO 2-20ZnO-5Na 2O) comparison of Raman curve.
Fig. 7 is that erbium ion is at glass (55GeO of the present invention 2-20PbO-10BaO-10ZnO-5K 2O-1.0Yb 2O 3-0.2Er 2O 3, 45TeO 2-20GeO 2-20PbO-10BaO-10ZnO-5K 2O-1.0Yb 2O 3-0.2Er 2O 3) and tellurate glass (75TeO 2-20ZnO-5Na 2O-1.0Yb 2O 3-0.2Er 2O 3) in the comparison of up-conversion luminescence intensity.
Embodiment
The invention will be further described below by specific embodiment, but should not limit protection scope of the present invention with this.
Table 1 has provided component and the molar percentage thereof that the present invention has the germanate laser glass of up-conversion luminescence and has formed
Table 1
Component composition range (mole is formed)
GeO 2 10％≤GeO 2≤55％
TeO 2 0＜TeO 2≤45％
PbO+Bi 2O 3 PbO+Bi 2O 3＝20％
BaO BaO＝10％
ZnO ZnO＝10％
R 2O(R＝Li，Na，K) R 2O＝5％
Yb 3++Tm 3++Er 3+ 0＜Yb 3++Tm 3++Er 3+＜2
According to purpose of the present invention, this glass is with TeO 2Be the system of glass-former, its compositing range is 0～45mol%.With TeO 2In the glass for organizer, because tellurium atom has bigger atomic radius, it is strong that its Te-O key that forms with Sauerstoffatom has more weak key than other network organizer atom as: the valence bond of Si, B, P etc. and Sauerstoffatom formation.From the formation theory of glass as can be known: if the phase-splitting or the crystallization of the strong poor excessive or too small glass that all can cause of the key of network outer body and network organizer the glass.For tellurate glass,, need to add the network outer body of the bigger oxide compound of atomic radius as glass for the thermostability that realizes that it is higher.In addition, in order to realize higher up-conversion luminescence intensity, the network outer body that is added must have lower maximum phonon energy.So bigger WO of phonon energy 3, Mo 2O 3All be not suitable for joining in the tellurate glass Deng heavy metal oxide as network outer body.And PbO and Bi 2O 3Be the two heavy metal species oxide compounds of using always, Pb, Bi have bigger atomic radius, the more weak strong and lower maximum phonon energy of M-O key (is respectively 460cm -1And 500cm -1).With heavy metal oxide PbO or Bi 2O 3Or both molectrons are elected to be the main network outer body composition of forming when front glass, and it consists of 20mol%.Outside the removing heavy metals oxide compound, BaO and ZnO also are the network outer body compounds that meets above-mentioned condition, and ZnO can also form tetrahedral structure with oxygen, to increase the intensity of network in the glass.Therefore the secondary network ectosome composition of selecting one or several the molectron among BaO, the ZnO to form as glass, its compositing range is 20mol%.
Utilize mixed alkali effect equally also can realize the stability of reinforcing glass, above selected network outer body all be the bigger metal ion of atomic radius, add that network organizer atom Te itself also has bigger atomic radius, therefore in above-mentioned glass, exist bigger space, this has reduced the stability of glass, therefore also needs to select the less oxide compound of some atomic radiuses to join as network outer body and makes it form stable network structure in the glass.By component adjustment experiment, the network-modifying ion of the little atomic radius that is added is Li -, Na -, K -, it consists of 5mol%.
By above-mentioned component adjustment, the composition range of glass that satisfies the wire drawing requirement is very narrow, only by one, two kind of glass forms and satisfies the wire drawing requirement, is unfavorable for the performance of glass is improved, there is the crystallization peak in most of glass in the wire-drawing temperature zone.For further stabilized glass, enlarge the formation scope of glass.Need in above-mentioned tellurate glass, add stable oxide more, Al 2O 3Once be used for stable silicon hydrochlorate, phosphate glass as intermediate.But in tellurate glass, Al 2O 3Add phase-splitting and the serious crystallization that affiliation causes glass.Other legacy network organizer is (as SiO 2, B 2O 3, P 2O 5Though) can play the effect of stabilized glass, they all have the phonon energy bigger than tellurate glass, are unfavorable for realizing the last switching emission of rare earth ion.
In numerous oxide glass organizers, germanium atom has bigger atomic radius (same Si, B, P compare), and the bismuth germanate glass that is formed by germanium oxide has excellent mechanical property, better chemical and thermostability.And can form stable glass with germanium oxide equally for the selected network outer body of tellurate glass.In addition, more interesting is that germanium oxide has the maximum phonon energy close with tellurium oxide.Germanium oxide is incorporated in the tellurate glass, can melts the interlacing network structure of formation mutually, can improve the basic physical properties, particularly thermostability of glass greatly with tellurium oxide.By exploring and the adjusting process prescription, it is as shown in table 1 that the glass compositing formula of fibre-optical drawing is changed in more satisfactory can being used for of seeking.
Describe below in conjunction with experimental result:
That shown in Figure 1 is existing tellurate glass (75TeO 2-20ZnO-5Na 2O-1Er 2O 3) differential thermal analysis curve, tellurate glass has serious crystallization phenomenon in 480-600 ℃ of wire-drawing temperature zone as can be seen.
Shown in Figure 2 is the differential thermal analysis curve of germanium lead glass of the present invention, and its glass composition sees Table 2.
Table 2
Sample composition Tg (℃) Tx (℃) Tc (℃)
75TeO 2-20ZnO-5Na 2O-1Er 2O 3 330 560 580
Sample-1 55GeO 2-20PbO-10BaO-10ZnO-5K 2O- 430 / /
1Er 2O 3
Sample-2 45TeO 2-10GeO 2-20PbO-10BaO-10ZnO- 335 / /
5K 2O-1Er 2O 3
As can be seen: along with germanium oxide replaces tellurium oxide, in wire-drawing temperature 500-680 ℃ scope, the crystallization peak does not appear in tellurium germanium lead glass of the present invention.Rare earth ion doped tellurium germanium lead glass is incubated 2 hours in the wire-drawing temperature scope, does not find the crystallization phenomenon, therefore satisfy the requirement of drawing process by range estimation.
Shown in Figure 3 is the glass differential thermal analysis curve that the present invention has different plumbous bi contents, and its composition sees Table 3.
Table 3
Sample composition Tg (℃) Tx (℃) Tc (℃)
Sample-3 55GeO 2-20PbO-10BaO-10ZnO-5K 2O-1Er 2O 3 430 / /
Sample-4 55GeO 2-10PbO-10BiO 3/2-10BaO-10ZnO-5K 2O- 431 / /
1Er 2O 3
Sample-5 55GeO 2-20BiO 3/2-10BaO-10ZnO-5K 2O-1Er 2O 3 433 / /
Sample-6 45TeO 2-10GeO 2-20PbO-10BaO-10ZnO-5K 2O-1 335 / /
Er 2O 3
Sample-7 45TeO 2-10GeO 2-10PbO-10BiO 3/2-10BaO-10Zn 341 / /
O-5K 2O-1Er 2O 3
Sample-8 45TeO 2-10GeO 2-20BiO 3/2-10BaO-10ZnO-5K 2O 345 / /
-1Er 2O 3
As can be seen: no matter be that along with the replacement of bismuth to lead, the transition temperature of glass all increases at the germanium lead glass or in tellurium germanium lead glass.In the glass of the low germanium of high tellurium, along with the replacement of bismuth to lead, glass has a little relaxation peak (Sample-8) in the wire-drawing temperature scope.Rare earth ion doped this kind glass is incubated 2 hours in the wire-drawing temperature scope, finds the glass devitrification by range estimation.Therefore in high tellurium glass, when replacing lead with bismuth, the form that should take part to replace is to avoid crystallization occurring in the wire-drawing temperature scope.
Shown in Figure 4 is the glass differential thermal analysis curve that the present invention contains the Different Alkali metal species, and the composition of glass sees Table 4.
Table 4
Sample composition Tg (℃) Tx (℃) Tc (℃)
Sample-9 55GeO 2-20PbO-10BaO-10ZnO-5Li 2O-1Er 2 426 / /
O 3
Sample-10 55GeO 2-20PbO-10BaO-10ZnO-5Na 2O-1Er 2 427 / /
O 3
Sample-11 55GeO 2-20PbO-10BaO-10ZnO-5K 2O-1Er 2 430 / /
O 3
Sample-12 55GeO 2-20BiO 3/2-10BaO-10ZnO-5Li 2O-1E 432 / /
r 2O 3
Sample-13 55GeO 2-20BiO 3/2-10BaO-10ZnO-5Na 2O-1 427 / /
Er 2O 3
Sample-14 55GeO 2-20BiO 3/2-10BaO-10ZnO-5K 2O-1Er 2?433 / /
O 3
Sample-15 45TeO 2-10GeO 2-20PbO-10BaO-10ZnO- 336 / /
5Li 2O-1Er 2O 3
Sample-16 45TeO 2-10GeO 2-20PbO-10BaO-10ZnO- 336 / /
5Na 2O-1Er 2O 3
Sample-17 45TeO 2-10GeO 2-20PbO-10BaO-10ZnO- 335 / /
5K 2O-1Er 2O 3
Sample-18 45TeO 2-10GeO 2-20BiO 3/2-10BaO-10ZnO- 340 / /
5Li 2O-1Er 2O 3
Sample-19 45TeO 2-10GeO 2-20BiO 3/2-10BaO-10ZnO- 342 485 545
5Na 2O-1Er 2O 3
Sample-20 45TeO 2-10GeO 2-20BiO 3/2-10BaO-10ZnO- 345 / /
5K 2O-1Er 2O 3
By table as can be seen: the mutual replacement between the basic metal such as lithium, sodium, potassium does not influence the thermal characteristics of glass.
Shown in Figure 5 is the DTA on Glass curve that the present invention contains different rare earth ions, and the composition of glass sees Table 5.
Table 5
Sample composition Tg (℃) Tx (℃) Tc (℃)
Sample-21 55GeO 2-20PbO-10BaO-10ZnO-5K 2O-1.0Er 2O 3 430 / /
Sample-22 55GeO 2-20PbO-10BaO-10ZnO-5K 2O-2.0Er 2O 3 435 / /
Sample-23 45TeO 2-10GeO 2-20PbO-10BaO-10ZnO-5K 2O- 335 / /
1.0Er 2O 3
Sample-24 45TeO 2-10GeO 2-20PbO 348 476 510
-10BaO-10ZnO-5K 2O-2.0Er 2O 3
Sample-25 55GeO 2-20PbO-10BaO-10ZnO-5K 2O-1.0Yb 2O 3- 430 / /
0.1Tm 2O 3
Sample-26 55GeO 2-20BiO 3/2-10BaO-10ZnO-5K 2O-1.0Yb 2O 3- 433 / /
0.1Tm 2O 3
Sample-27 45TeO 2-10GeO 2-20PbO-10BaO-10ZnO-5K 2O- 335 / /
1.0Yb 2O 3-0.1Tm 2O 3
Sample-28 45TeO 2-10GeO 2-20BiO 3/2-10BaO-10ZnO-5K 2O- 345 / /
1.0Yb 2O 3-0.1Tm 2O 3
Annotate: (1) Tg represents the transition temperature of glass; Tx represents that crystallization begins temperature; Tc represents the crystallization peak temperature
(2) Sample-1,3,11 and 21 is a same sample; Sample-2,6,17 and 23 is a same sample;
Sample-5,14 is a same sample; Sample-8,20 is a same sample.
Because rare earth ion has close ionic radius, and in glass, all be in the position of calking, so glass is more or less the same to the solubleness of rare earth ion, only provides Er here as network outer body 2O 3Influence to glass heat stability.As can be seen: work as Er 2O 3Concentration when reaching 2mol%, the crystallization peak has appearred in glass in the wire-drawing temperature scope.But when the concentration of rare earth ion during less than 2mol% (as 1mol%), rare earth ion is to the almost not influence of thermal characteristics of host glass.
Fig. 6 is tellurium germanium host glass (55GeO 2-20PbO-10BaO-10ZnO-5K 2O-1.0Yb 2O 3-0.2Er 2O 3, 45TeO 2-20GeO 2-20PbO-10BaO-10ZnO-5K 2O-1.0Yb 2O 3-0.2Er 2O 3) and tellurate host glass (75TeO 2-20ZnO-5Na 2O) comparison of Raman curve.Replace the increase of tellurium oxide amount as can be seen along with germanium oxide, the maximum phonon energy blue shift of host glass, this is disadvantageous to last conversion.And the interpolation of small amounts germanium is little to the influence of the maximum phonon energy of host glass.
That shown in Figure 7 is tellurium germanite glass (55GeO 2-20PbO-10BaO-10ZnO-5K 2O-1.0Yb 2O 3-0.2Er 2O 3, 45TeO 2-20GeO 2-20PbO-10BaO-10ZnO-5K 2O-1.0Yb 2O 3-0.2Er 2O 3) and tellurate glass (75TeO 2-20ZnO-5Na 2O-1.0Yb 2O 3-0.2Er 2O 3) the up-conversion luminescence intensity curve.As can be seen along with the increase of Germania content, on change green glow intensity reduce.In the glass that adds small amounts germanium, on change green glow luminous intensity be higher than the intensity of ruddiness far away.In the application of up-conversion lasing, on change green glow and application prospects more arranged than ruddiness.

Claims (4)

1, a kind of germanate laser glass with up-conversion luminescence is characterized in that this glass comprises following composition:
Component composition range (mol%)
GeO 2 10≤GeO 2≤55
TeO 2 0＜TeO 2≤45
PbO+Bi 2O 3 PbO+Bi 2O 3＝20
BaO BaO＝10
ZnO ZnO＝10
R 2O(R＝Li，Na，K) R 2O＝5
Yb 3++Tm 3++Er 3+ 0＜Yb 3++Tm 3++Er 3+＜2
2, the germanate laser glass with up-conversion luminescence according to claim 1 is characterized in that described heavy metal oxide can be by PbO, Bi 2O 3Or these two kinds of combination of compounds bodies.
3, the germanate laser glass with up-conversion luminescence according to claim 1 is characterized in that described R 2O can be Li 2O, Na 2O or K 2O.
4, the germanate laser glass with up-conversion luminescence according to claim 1 is characterized in that described rare earth ion can be Yb 3+, Tm 3+, Er 3+Or its molectron.
CN 200410017066 2004-03-19 2004-03-19 Laser glass of germanate possessing upper transition luminescence Pending CN1562838A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN 200410017066 CN1562838A (en) 2004-03-19 2004-03-19 Laser glass of germanate possessing upper transition luminescence

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN 200410017066 CN1562838A (en) 2004-03-19 2004-03-19 Laser glass of germanate possessing upper transition luminescence

Publications (1)

Publication Number Publication Date
CN1562838A true CN1562838A (en) 2005-01-12

Family

ID=34478754

Family Applications (1)

Application Number Title Priority Date Filing Date
CN 200410017066 Pending CN1562838A (en) 2004-03-19 2004-03-19 Laser glass of germanate possessing upper transition luminescence

Country Status (1)

Country Link
CN (1) CN1562838A (en)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103086601A (en) * 2012-12-13 2013-05-08 昆明理工大学 Bismuth-doped germinate ultra wideband optical glass and preparation method thereof
CN103359939A (en) * 2012-03-27 2013-10-23 中国科学院西安光学精密机械研究所 Green-light-emitting tellurate glass and preparation method thereof
CN109320065A (en) * 2018-11-20 2019-02-12 广东工业大学 A kind of novel transition metal ion doping energy-saving glass and preparation method thereof

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103359939A (en) * 2012-03-27 2013-10-23 中国科学院西安光学精密机械研究所 Green-light-emitting tellurate glass and preparation method thereof
CN103086601A (en) * 2012-12-13 2013-05-08 昆明理工大学 Bismuth-doped germinate ultra wideband optical glass and preparation method thereof
CN103086601B (en) * 2012-12-13 2015-06-03 昆明理工大学 Bismuth-doped germinate ultra wideband optical glass and preparation method thereof
CN109320065A (en) * 2018-11-20 2019-02-12 广东工业大学 A kind of novel transition metal ion doping energy-saving glass and preparation method thereof

Similar Documents

Publication Publication Date Title
CN101492248B (en) 2 [mu]m laser output thulium tellurate doped glass and optical fiber, and producing method thereof
CN1807304A (en) Glass beads and uses thereof
CN111377609B (en) Preparation method of transparent glass with mid-infrared 3.9 mu m luminescence characteristic at room temperature
CN1876589A (en) Lead and arsenic free optical lanthanum borate glass
CN1291173A (en) Antimony oxide glass with optical activity
CN100513339C (en) Rare earth doped gallium germanium bismuth lead luminous glass material and its preparation method and uses
CN102659313B (en) Near-infrared broadband luminescence erbium and thulium-co-doped bismuthate laser glass and preparation method thereof
US5240885A (en) Rare earth-doped, stabilized cadmium halide glasses
CN103011593A (en) Erbium neodymium ion co-doped tellurium fluoride glass for emitting 2.7 microns of intermediate infrared light
CN103771710A (en) Rare earth doped near-infrared luminescent glass and preparation method thereof
CN104230167A (en) Quantum dot doped glass and preparation method thereof
CN101870557A (en) Preparation method of germanium tellurite glass optical prefabricated rod output by green ray
CN1562838A (en) Laser glass of germanate possessing upper transition luminescence
CN101121574B (en) Thulium adulterated germanate laser glass and preparation method thereof
CN1313403C (en) Light amplified erbium Ytterbium codoped multi-component oxide glass and method for manufacturing same
US5346865A (en) Rare earth-doped, stabilized cadmium halide glasses
CN103159404A (en) Boron-free and alkali-free silicate laser glass for 2mu m output and preparation method thereof
CN1562833A (en) Oxygen-fluorin silicic acid glass with Er/Yb heavy metal mixed into, and preparation method
CN105271730B (en) A kind of multicolor emission tellurium bismuth titanium glass and preparation method thereof
CN1391536A (en) Fluorotellurite amplifier glasses
CN103058516A (en) High-concentration erbium ion doped tellurium tungstate glass capable of emitting light at mid-infrared 2.7 microns
CN1233580C (en) Tm/Yb codoped oxyfluoro tellurate glass and its preparation method
CN111170633A (en) Thulium-ytterbium co-doped phosphate up-conversion luminescent glass and preparation method and application thereof
CN1636906A (en) Er/Yb doped tellurate oxychloride glass and its prepn process
CN107162427A (en) A kind of high power semiconductor light source activation glass ceramics and its preparation method and application

Legal Events

Date Code Title Description
C06 Publication
PB01 Publication
C10 Entry into substantive examination
SE01 Entry into force of request for substantive examination
C02 Deemed withdrawal of patent application after publication (patent law 2001)
WD01 Invention patent application deemed withdrawn after publication