CH 24. Solids • Defects – Non-stoichiometry, Ionic Conductivity • Cooperative Phenomenon – Magnetism, Piezoelectricity, Superconductivity • Topochemical Reactions – Intercalation chemistry Defect types Shottky (vacancy) Frenkel Substitution (interstitial) NaCl TiO AgCl Shottky vacancy 10-12 M at 130 °C (1 / 1014 units) Shottky vacancy ≈10 M at 25 °C (1 / 10 units) Frenkel interstitial Ag+ 2 F-centers Δ NaCl Na1+xCl green/yellow epr “free e-” Na NaCl Δ NaKxCl green/yellow same K Δ KCl KCl K1+xCl violet KNaxCl violet K Δ Na 3 Defect concentrations 4 Intrinsic vs extrinsic defects Intrinsic – thermodynamic effect, defects are favored by G min Extrinisic – defects introduced by sample prep conditions, dopants, impurities (intentional or unintentional) Examples: n-doped Si (m) “n-doped Si” Li2O in NiO LixNi(III)xNi(II)1-xO introduce Li+ to change electronic properties 5 Extended defects Shear planes in WO3-x 6 Non-stoichiometric oxides Mo8O23 7 Non-stoichiometry 8 Ionic Conduction Microscopic view: Correlation of defects with mechanism Concentration gradients: Fick’s Law 9 Ionic Conduction Macroscopic view: Measure ionic = i (Di, qi, ci) i i = D= q = c = all significant charge carriers diffusion coefficient (related to mobility) ion charge ion concentration Arrhenius behavior: = o exp (-Ea/RT) ln vs 1/T is linear with slope = Ea/R 10 AgI -AgI wurtzite (AaBb)n , 146 C -AgI bcc I array with Ag+ statistically distributed in CN=3,4 sites ~ 1Ω-1cm-1 , Ea ~0.05 eV when -AgI melts at 550 C, the Ag+ decreases! 11 Ag2HgI4 and RbAg4I5 RbAg4I5 is single phase from RT to 500 C ~ bcc I array ~ 0.25 Scm-1; Ea~0.07eV Close packed I lattice with 3/8 Td sites occupied order/disorder transition at 50 C (break in data) VTF behavior - lattice activation contributes to conduction mechanism, so Arrhenius plot is curved 12 Calcium-stabilized zirconia CaxZr1xO2x□x □ = O2 ion vacancy Fluorite structure (8,4) (AabBbcCca)n (O2) ~104 at 500°C 13 Solid oxide fuel cell / sensor Concentration cell gas sample Air 2O2 O2 + 4e 4e + O2 2O2 O2 sensor in auto exhaust E log pO2 (sample) / pO2 (air) 160 torr 2H2 + 202 2H2O + 4e 4e + O 2 202 14 Na-’’-alumina (Na+) ~10 Scm-1 at 300 C 15 D for some ion conductors 16 1st row TM MOx compounds 17 FeO1.04-1.17 3Fe2+ O2 Oh sites 2Fe3+ + □ (cation vacancy) Td sites Oh sites Aggregate to form extended defect CoO1.0 – 1.01 NiO1.0 – 1.001 harder to oxidize to M3+ LixNi1-x/2O CuO1.00 only x ~ 0.01 add Li+, Ni2+ Ni3+ TiOx MnOx can also have x > 1, but also x < 1 (anion vacancies) 18 TiOx electronic structure 19 Magnetism diamagnetism – only e pairs, weak repulsion of magnetic field (H) X is small and negative ex: SiO2, CaO Χ = magnetic susceptibility = F / H d = magnetic moment F = sample formula wt H = applied magnetic field D = sample density paramagnetism – unpaired e with random orientation, strong attraction to H X = C / (T+ Θ) Curie-Weiss law C = Curie constant C 2 N(N+2) N = # unpaired spins 20 Magnetism ex: Fe3+ in aq solution or Fe(NO3)3 isolated mag. moments alignment is only induced by applied field, H 21 Ferromagnetism all mag. moments (e spins) spontaneously oriented in parallel direction () often due to direct M-M interactions (d –d orbital overlaps) ex: -Fe Ni bcc along [100] Fe is d6s2 N (obs) = 2.2 fcc along [111] Ni is d8s2 Tc = Curie temperature = temp for magnetic order (ferromagnetic / disorder (paramagnetic) transition measure of strength of interaction between spins -Fe Tc = 760 C (note that Fe bcc fcc phase transition is 906C) 22 Antiferromagnetism spins align antiparallel () Usually due to superexchange coupling (M-L-M interaction) Ex: NiO TN = Neel temp = temp for antiferromagnetic / paramagnetic transition NiO TN = 250 C Ferrimagnetism – spins antiparallel, but don’t cancel 23 Magnetic ordering in FeO 293 K TN ≈ 200 K 4.2 K 24 Curie plots 25 Hysteresis / domain structure Weiss domains Hard vs. soft For magnetic data storage (floppies/hard drives/tapes) Ex: hard – hard/floppy disks want high residual M but small coercive force soft – record heads 26 Spinels Normal spinel AB2O4 A(II) B(III) O2 ccp array A in 1/8 Td sites B in ½ Oh sites Ex: MgAl2O4 or ZnFe2O4 Inverse spinel B[AB]O4 A in Oh sites, ½ B in Td sites, ½ B in Oh sites Ex: NiFe2O4 = Fe[NiFe]O4 Fe3O4 = Fe(III)[Fe(II)Fe(III)]O4 27 Spinels = occupancy factor (fraction of B cations in Td sites) range is = 0 (normal) to 0.5 (full inverse) A B Mg2+ Mn2+ Fe2+ Co2+ Ni2+ Cu2+ Zn2+ d10 d0 d5 d6 d7 d8 d9 Al3+ d0 0 0 0 0 0.38 0 Cr3+ d3 0 0 0 0 0 0 Mn3+ d4 0 Fe3+ d5 0.45 Co3+ d6 0 0 0.1 0.5 0.5 0.5 0 0.5 0 0 28 Magnetism in spinels ZnFe2O4 Zn(II) Td sites d10 (N=O) Fe(III) Oh sites d5 (N = 5) antiferromagnetic TN = 10K weak superexchange coupling between Oh sites in spinel λ =0.5 (inverse spinel) NiFe2O4 Fe[NiFe]O4 Oh sites d8 (N = 2) ½ Fe(III) Oh sites d5 (N = 5) ½ Fe(III) d5 (N = 5) Ni(II) Td sites µ = √2(2+1)µb = 2.5µb ferrimagnet TN = 585 C (strong coupling between Oh and Td sites) 29 Magnetism in spinels - Fe2O3 inverse defect spinel, used in disk storage ~5 m film deposited on plastic tape Fe(III)[Fe1.67(III)□0.33]O4 Td Oh medium-hard ferrimagnet 1 Fe(III) Td d5 N=5 1.67 Fe(III) Oh d5 N=5 30 ReO3 31 Perovskites (CaTiO3) Simple perovskites have an ABX3 stoichiometry. The A cation and X anions, taken together, comprise a close-packed array, with B cations filling 1/4 of the octahedral sites. An ordered AA’BX3 perovskite 32 Perovskites ABX3 CN A = 12 B = 6 X = 2 common for oxides and fluorides (ex NaFeF3) 33 Ruddlesden-Popper phases Ca4Mn3O10 K2NiF4 Sr3Fe2O7 34 YBa2Cu3O7 35 Tl2Ba3Ca2Cu3O10 36 Ferroelectrics Ideal perovskite structure has cubic symmetry (centrosymmetric) But structures are often distorted to be non-centrosymmetric These can be ferroelectric In BaTiO3 , the Ti cation is a little smaller than the Oh site (Ti-O ~ 1.95Å), and is displaced ~0.1Å off site center towards an oxide ligand, forming a dipole Above Tc (=120 C) the dipoles are randomly oriented, and structure is cubic (paraelectic) Below Tc - all dipoles orient along the same direction (ferroelectric) Note: ferroelectricity is named by analogy to ferromagnetism, but it is not common for Fe-containing materials Also: antiferroelectric ferrielectric one difference – dipole ordering is tied to structural change 37 BaTiO3 Dielectric constant vs temp 38 Ferro/piezoelectrics CaTiO3 is not ferroelectric, the smaller Ca2+ ion reduces Oh site and Ti4+ is not small enough to displace off center BaxSr1x TiO3 (BST) is ferroelectric with a lower Tc, so the max in ε’ occurs at a lower temp. It’s used in dynamic RAM (DRAM) capacitor elements ε’ Ex: water 80 TiO2, MgTiO3 10–100 BST ferroelectrics 4000-8000 piezoelectrics – crystals polarize under applied mechanical stress and vice versa (applied E across crystal generates lattice strain) crystals must be noncentrosymmetric P = d P = polarization, σ = mechanical stress 39 Piezoelectrics Piezoelectrics: ex: quartz crystal, BaTiO3 PbZrxTi1xO3 (PZT) actuators, x~0.5 highest d positioning - apply E induce Qz transducers (pressure measurement) use from sensed pressure to produce E signal 40 Two-zone transport 41 MX2 42 Layered structures MO2 and MS2 structures and intercalation Two basic structure types with different cation coordnation geometries 1. CdI2 structure, cations in Oh sites, filling alternate layers (AcB)n 1T CdI2, TiS2, TaS2, ZrS2, Mg(OH)2 (brucite) Polytypes, ex: (AcB CbA BaC)n 3R 2. MoS2 structure, cations in trig prismatic sites (D3h) , filling alternate layers MoS2, NbS2 (AbA BaB)n 2H (AbA CbC)n (Aba BcB CaC)n 43 Electrochemical intercalation 44 Intercalation compounds 45 TaS2 intercalation Intercalate ion = [Fe6S8(P(C2H5)3)6]2+ 46 DOS diagrams for MS2 eg e” e’ t2g a1’ 47 Peierl’s distortion Peierl’s distortion: polyacetylene K2Pt(CN)4Br0.3 3H2O (KCP) Charge density waves: TaS2 48 Charge density waves To observe CDW typical tunnelling parameters of 2-3 nA and 10-20 mV gap voltage were observed. The atomic lattice can be seen simul- taneously when the current is increased to higher values (30 - 40 nA). TaS2 (and TaSe2) exhibit an electronic phase transition from a normal into a condensed state which is called the Charge Density Wave (CDW) state. The transition is caused by an electron-phonon coupling. STM images of TaS2 show a triangular atomic lattice (a0=0.33 nm) with a superimposed CDW lattice of about 3.5 a0. The CDW lattice is rotated 11° with respect to the atomic lattice. http://www.nanosurf.com 49 LiCoO2 50 Electrode and cell potentials http://www.mpoweruk.com/performance.htm 51 Li+ battery chemistry Cathode LiCoO2 Li1-xCoO2 + xLi+ + xeAnode 6C + Li+ + e- C6Li Electrolyte Organic solvent with LiPF6 52 Insertion hosts 53 Framework solids 54 Molecular sieves 55 Pillared clays 56 Pillared structures http://www.cem.msu.edu/~pinnweb/research-na.htm Oregon State University 57 Ag(bipy)NO3 58 Fe(III)4[Fe(II)(CN)6]3 Prussian blue 59 Graphite Intercalation Expands about 10% along z Li+ occupies hexagon centers of non-adjacent hexagons Graphite reduction at 0.1-0.5 V vs Li+/Li Theoretical capacity: Li metal > 1000 mAh/g C6Li 370 60 Structures: borate chelate GIC’s 1.13 CxB(O2C2(CF3)4)2 Stage 1 0.85 nm 1.12 CxB(O2C2O(CF3)2)2 Blue: obs Pink: calc Stage 2 0.78 nm T Unexpected anion orientation - long axis to sheets 61