1.4 Composition: congruent and stoichiometric
L1 A range, not a formula
“LiNbO3” is a range, not a formula. The crystal is stable from roughly 47 to 50 mol% Li2O, always on the lithium-poor side of the ideal 50% P-comp. When the melt and the growing crystal have the same composition, the crystal grows uniform from seed to tail. For LiNbO3 that congruent point is about 48.4–48.5 mol% Li2O, a lithium-to-niobium ratio of 0.94 P-comp, so in nearly every commercial crystal about one lithium site in twenty holds no lithium derived.
Removing that deficit changes the crystal: Curie temperature up by about 60 °C, UV absorption edge about 17 nm toward shorter wavelengths derived, the field needed to flip the polarization several-fold lower, and the built-in bias field gone (1.3, 1.8). Stoichiometric crystal cannot be pulled from a stoichiometric melt; it needs one of the growth routes in L2.
| [Li]/[Nb], R1 | 0.9399 | derived |
| [Li]/([Li]+[Nb]), R2 | 0.4845 | derived |
| x, per formula unit | 0.0101 | derived |
| NbLi, of Li sites | 1.01 % | derived |
| VLi, of Li sites | 4.05 % | derived |
| VNb, of Nb sites | 0.00 % | derived |
| Tc, Iyi fit | 1141.5 °C | P-comp |
| Tc, Bordui fit | 1145.9 °C | P-comp |
| Tm, congruent | 1255 °C | P-comp |
| λ20 (α = 20 cm−1) | 320.2 nm | derived |
| λ15 (α = 15 cm−1) | 321.8 nm | derived |
| Ec at c | 21 kV/mm | P-comp |
| Eint at c | 2.2–3.4 kV/mm | P-comp |
| Anchor | c span | Ec | Eint |
|---|---|---|---|
| congruent | 48.38–48.6 | 21 kV/mm P-comp | 2.2–3.4 kV/mm misprint |
| near-stoich. | 49.8–50.0 | 6.0–6.5 / 2.1–2.5 kV/mm conflict | → 0 P-comp |
T / °C 1100 1150 1200 1250 1300 |----+----|----+----|----+----|----+----| c 48.45 ========##------------------------------- Tc CLN ^ Tc nSLN ^ Tm CLN ^
λ / nm 300 305 310 315 320 325 |---+---|---+---|---+---|---+---|---+---| α>20/cm ################################|........ α>15/cm ###################################|.....
................................ ................... ......#.... ................................ .#................. ............ .............#...... .......... ............................. .. .............. ................. ... .#.............. ........... . ................. ............ .... .......................... ......... ...................... ...............................
:::::::::::::::::::::::::::::::: :::::::::::::::::::::::::::::::: :::::::::::::::::::::::::::::::: :::::::::::::::::::::::::::::::: :::::::::::::::::::::::::::::::: :::::::::::::::::::::::::::::::: :::::::::::::::::::::::::::::::: :::::::::::::::::::::::::::::::: :::::::::::::::::::::::::::::::: :::::::::::::::::::::::::::::::: :::::::::::::::::::::::::::::::: ::::::::::::::::::::::::::::::::
- [Li]/[Nb]
- 0.9399
- Antisites x per formula unit
- 0.0101
Lattice sites
derivedCurie temperature
P-comp- Tc, Iyi / Bordui fit
- 1141.5 °C / 1145.9 °C
- Markers
- P-comp
Stripes: the ferroelectric phase, where ±z domains exist; it ends at Tc. Waves: congruent crystal is molten above 1255 °C.
UV absorption edge
derived- λ20 / λ15
- 320.2 nm / 321.8 nm
22 °C, E ∥ c, k ⊥ c. Hatched: ultraviolet (below 400 nm), invisible. Shaded: absorption above 20 cm−1. Solid line λ20, dashed λ15.
Switching fields
- Ec
- 21 kV/mm P-comp
- Eint
- 2.2–3.4 kV/mm misprint
- Ec
- 6.0–6.5 or 2.1–2.5 kV/mm conflict
- Eint
- → 0 P-comp
Values light only while c sits in an anchor span; between them no source gives a value. P-comp
L2 Composition data
| Quantity | Value | Status |
|---|---|---|
| Phase diagram Li2O–Nb2O5 | Reisman and Holtzberg 1958 | P |
| Congruent composition | 48.45 mol% Li2O, [Li]/[Nb] = 0.94 | P-comp |
| Congruent composition | 48.6 mol% Li2O; room-temperature solid solution 48–50 mol% | P(abs) |
| Congruent composition | Li/Nb mole ratio 0.946 | P |
| Congruent composition | C = Li2O/(Li2O + Nb2O5) = 0.484 | P(abs) |
| Congruent composition | 48.38 ± 0.01 mol%; reference point of the UV-edge formula | V P-comp |
| Solid-solution width | about 6 mol% above 1150 °C; diffuse liquidus maximum at about 48.45 mol% | P-comp |
| Required uniformity for optics | [Li]/[Nb] fixed within 10−3 | P-comp |
| Melt to crystal | c = 48.5 + 0.3436 (cmelt − 48.5) − 0.02897 (cmelt − 48.5)2, valid 45 < cmelt < 52 mol%, ±0.3 mol% | P-comp |
Ratios
Composition ratios in the literature: R1 = [Li]/[Nb], R2 = [Li]/([Li] + [Nb]) = c/100 derived. At c = 48.45 mol%, R1 = 0.940 derived. Volk & Wöhlecke 2008 prints R1 = 0.969 next to R2 = 0.4845 on p. 5, inconsistent with its own 0.94 on p. 10 misprint.
UV absorption edge vs composition
22 °C, E ∥ c, k ⊥ c, x = c − 48.38 mol% P-comp:
λ20 = 320.4 − 1.829 x − 5.485 x2 nm (absorption 20 cm−1) λ15 = 321.9 − 1.597 x − 5.745 x2 nm (absorption 15 cm−1)
| c (mol% Li2O) | λ20 | λ15 | Status |
|---|---|---|---|
| 48.38 | 320.4 nm | 321.9 nm | derived |
| 49.00 | 317.2 nm | 318.7 nm | derived |
| 49.50 | 311.5 nm | 312.9 nm | derived |
| 50.00 | 303.0 nm | 304.2 nm | derived |
Above 49.5 mol%, 0.1 mol% maps to about 2 nm P-comp.
Growth routes to near-stoichiometric LiNbO3 (all reported 1992–1997)
| Method | Principle | Reported parameters | Status |
|---|---|---|---|
| Vapor transport equilibration (VTE) | crystal plate and Li-rich powder in one Pt crucible, no contact; Li diffuses in | > 1000 °C for days; plates < 1 mm, up to 3 mm reported; “extremely slow lithium diffusivity” for Li-poor targets | P-comp P(abs) |
| Double-crucible Czochralski (DCCZ) | pull from an Li-rich inner melt (about 58–60 mol% Li2O) in equilibrium with near-stoichiometric solid; stoichiometric powder fed continuously to the outer crucible, weight-controlled | – | P-comp P |
| Growth from K2O-containing melt | melt with up to 10% K2O; negligible K in the crystal | compositions 49.95 mol% or more | P-comp P |
| Top-seeded solution growth (TSSG) | same chemistry treated as a high-temperature solution | boules 20 mm diameter | P-comp P |
L3 How it is measured
Methods. Non-optical: chemical analysis, Tc, density, NMR and EPR linewidths, diffraction. Optical: UV edge, OH-band shape, Raman linewidths, phase-matching temperature; optical methods reach 0.1 mol% absolute and about 0.01 mol% relative accuracy P-comp P(abs). The UV-edge method needs a reflection correction of about 1 nm and fails when an impurity such as Fe absorbs near the edge P-comp. For near-stoichiometric crystal the intensity ratio of the OH components at 3480 and 3465 cm−1 decreases linearly with Li2O from 49.7 to 50 mol% P-comp.
Why 48.38 vs 48.45 vs 48.6. The congruent point depends on how the melt composition was determined, and on the oxygen content of the Nb2O5 feedstock, which may be oxygen-deficient P-comp. The L2 table gives each value with its source.
Defect models in the dial. The Li-site vacancy model compensates each NbLi with four Li vacancies; the Nb-site vacancy model compensates five NbLi with four Nb vacancies. Both predict the same R1 at every c, so composition alone cannot decide between them P-comp; the evidence is in 1.5. The dial's anchors for Ec and Eint come from 1.8.
Sources
- Volk & Wöhlecke 2008T. Volk, M. Woehlecke, Lithium Niobate: Defects, Photorefraction and Ferroelectric Switching, Springer Series in Materials Science 115 (Springer, Berlin Heidelberg, 2008). doi:10.1007/978-3-540-70766-0
- Iyi et al. 1992N. Iyi, K. Kitamura, F. Izumi, J. K. Yamamoto, T. Hayashi, H. Asano, S. Kimura, "Comparative study of defect structures in lithium niobate with different compositions", J. Solid State Chem. 101, 340-352 (1992). doi:10.1016/0022-4596(92)90189-3
- Bordui et al. 1992P. F. Bordui, R. G. Norwood, D. H. Jundt, M. M. Fejer, "Preparation and characterization of off-congruent lithium niobate crystals", J. Appl. Phys. 71, 875-879 (1992). doi:10.1063/1.351308
- Gopalan et al. 1998V. Gopalan, T. E. Mitchell, Y. Furukawa, K. Kitamura, "The role of nonstoichiometry in 180 ° domain switching of LiNbO3 crystals", Appl. Phys. Lett. 72, 1981-1983 (1998). doi:10.1063/1.121491
- Chen et al. 2001Y.-L. Chen, J.-J. Xu, X.-J. Chen, Y.-F. Kong, G.-Y. Zhang, "Domain reversion process in near-stoichiometric LiNbO3 crystals", Opt. Commun. 188, 359-364 (2001). doi:10.1016/S0030-4018(00)01137-8
- Crystal Technology 1999Crystal Technology Inc., "LiNbO3 material properties", data sheet DC-12 8/99 (congruent, 48.38 mol% Li2O).
- Carruthers et al. 1971J. R. Carruthers, G. E. Peterson, M. Grasso, P. M. Bridenbaugh, "Nonstoichiometry and crystal growth of lithium niobate", J. Appl. Phys. 42, 1846-1851 (1971). doi:10.1063/1.1660455
- Reisman & Holtzberg 1958A. Reisman, F. Holtzberg, "Heterogeneous equilibria in the systems Li2O-, Ag2O-Nb2O5 and oxide-models", J. Am. Chem. Soc. 80, 6503-6507 (1958). doi:10.1021/ja01557a010
- Weis & Gaylord 1985R. S. Weis, T. K. Gaylord, "Lithium niobate: Summary of physical properties and crystal structure", Appl. Phys. A 37, 191-203 (1985). doi:10.1007/BF00614817
- Kovacs et al. 1997L. Kovacs, G. Ruschhaupt, K. Polgar, G. Corradi, M. Woehlecke, "Composition dependence of the ultraviolet absorption edge in lithium niobate", Appl. Phys. Lett. 70, 2801-2803 (1997). doi:10.1063/1.119056
- Kitamura et al. 1992K. Kitamura, J. K. Yamamoto, N. Iyi, S. Kimura, T. Hayashi, "Stoichiometric LiNbO3 single crystal growth by double crucible Czochralski method using automatic powder supply system", J. Cryst. Growth 116, 327-332 (1992). doi:10.1016/0022-0248(92)90640-5
- Malovichko et al. 1993G. I. Malovichko, V. G. Grachev, E. P. Kokanyan, O. F. Schirmer, K. Betzler, B. Gather, F. Jermann, S. Klauer, U. Schlarb, M. Woehlecke, "Characterization of stoichiometric LiNbO3 grown from melts containing K2O", Appl. Phys. A 56, 103-108 (1993). doi:10.1007/BF00517674
- Polgar et al. 1997K. Polgar, A. Peter, L. Kovacs, G. Corradi, Zs. Szaller, "Growth of stoichiometric LiNbO3 single crystals by top seeded solution growth method", J. Cryst. Growth 177, 211-216 (1997). doi:10.1016/S0022-0248(96)01098-6