Switching effects

Franciszek Krok, Krystian Roleder, Krzysztof S. Szot

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ISBN/ISSN:

978-83-01-21695-5

DOI:

Wydawnictwo:

Wydawnictwo Naukowe PWN

Rok wydania:

2021

Liczba stron:

496

XML:ISBN/ISSN:

ONIX MARC21

Bibliografia:

Krok, Franciszek; Roleder, Krystian; Szot, Krzysztof S.. Switching effects. Red. . Warszawa: Wydawnictwo Naukowe PWN, 2021, 496 s. ISBN 978-83-01-21695-5

Bibliografia refWorks:

RT Book, Whole

SR Electronic(1)

A1 Krok, F.

A1 Roleder, K.

A1 Szot, K.S.

T1 Switching effects

PB Wydawnictwo Naukowe PWN

PP Warszawa

YR 2021

SN 978-83-01-21695-5

Bibliografia BibTex:

@Book{ 244073, author = "Krok, Franciszek and Roleder, Krystian and Szot, Krzysztof S.", editor = "", title = "Switching effects", publisher = "Wydawnictwo Naukowe PWN", year = "2021", address = "Warszawa", isbn = "978-83-01-21695-5" }

Bibliografia endNote:

TY - BOOK

AU - Krok, Franciszek

AU - Roleder, Krystian

AU - Szot, Krzysztof S.

ED -

TI - Switching effects

PB - Wydawnictwo Naukowe PWN

CY - Warszawa

PY - 2021

SN - 978-83-01-21695-5

ER -

Netografia (standard APA):

Krok, Franciszek; Roleder, Krystian; Szot, Krzysztof S.. Switching effects [baza danych online] Warszawa: Wydawnictwo Naukowe PWN, 2021 [dostęp: 06 05 2024]. Dostęp w Ibuk Libra: https://libra.ibuk.pl/reader/switching-effects-franciszek-krok-krystian-244073.

The oxides, especially the transition metal oxides, are a most important class of inorganic materials, being enormously interesting for basic research in solid-state physics, surface physics, defect chemistry, electrochemistry, and catalysis, to m...

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ISBN/ISSN:

978-83-01-21695-5

DOI:

Wydawnictwo:

Wydawnictwo Naukowe PWN

Rok wydania:

2021

Liczba stron:

496

XML:ISBN/ISSN:

ONIX MARC21

Introduction12
1. An Introduction to the Crystal Structures of Oxide Perovskites14
1.1. Atomic Displacements16
1.2. Octahedral Tilting24
1.3. Distortion Modes26
References29
2. Growth of ABO3 and BO2 Crystals31
2.1. Theory of Crystal Growth31
2.1.1. Equilibrium Conditions31
2.2. Phase Diagrams of Model Oxides. Major Challenges in Crystal Growth of Stoichiometric Oxide Crystals34
2.2.1. Gibbs Phase Rule34
2.2.2. Phase Diagrams35
2.2.3. Nonstoichiometric Oxides35
2.3. Techniques of Growth of Selected Binary and Ternary Oxide Crystals36
2.4. Typical Methods for Evaluation of Quality of Oxide Crystals41
2.4.1. Stoichiometric TiO242
2.4.2. Perovskite Structure42
References47
3. Defect Chemistry in Binary and Ternary Metal Oxides 52
3.1. Introduction52
3.2. Imperfect Crystals53
3.3. Quasi-chemical Defect Reactions54
3.4. Types of Point Defects55
3.5. Thermodynamic Approach55
3.6. Nonstoichiometry58
3.7. Aggregations of Point Defects and Extended Defects59
3.8. Ideal Point Defect Model62
3.8.1. Case of Ni1–yO62
3.8.2. Case of BaTiO3–y65
3.8.3. Case of Zirconia-based Materials68
3.8.4. Defect Structure of YSZ73
3.9. Debye-Hückel Defect Model74
3.9.1. Co1–yO Case74
3.10. Cluster Model78
3.10.1. Defect Clustering in the Wustite Phase78
3.11. Crystallographic Shearing81
3.12. Defect Structure of Titanium Dioxide82
3.12.1. Extended Defects in TiO286
3.13. Hydrogen Defects87
Acknowledgements88
References88
4. Self-Polarization of Ferroelectric Thin Films and Its Influence on the Film Properties93
4.1. Introduction94
4.2. Free Energy Functional95
4.3. Renormalized Free Energy and Properties for One Component Polarization P = PZ97
4.4. The Influence of Built-in Electric Field on the Properties of Ferroelectric Thin Films for the Case P = PZ100
4.5. Phase Diagrams with Electret State and Properties for the Case of Three Polarization Components104
4.6. Comparison with Experiment and Summary of Sec. 5 Results115
Conclusion118
References119
5. Lattice Dynamics of Perovskite Oxides 121
5.1. Introduction121
5.2. Early Attempts to Model Ferroelectric Perovskites122
5.3. Polarizability Effects in Perovskites125
5.4. The Polarizability Model for Perovskites127
5.5. Applications of the Model132
5.6. Precursor Effects to the Phase Transitions138
Conclusions147
References148
6. Metrology and Measurement Techniques 152
6.1. Electrical Properties of Nanoscale Solids152
6.1.1. Measurement of Electrical and Magnetic Material Properties153
6.1.2. The Piezoelectric Effect164
6.2. Design of Measurement Setups167
6.2.1. General Considerations167
6.2.2. Active Amplifier Circuits170
6.2.3. Measurement Methods for Ferroelectric Properties173
6.2.4. Laser Interferometers184
References189
7. Multiferroics 191
7.1. Abstract191
7.2. Introduction191
7.3. A Brief History of Magnetoelectrics and Multiferroics192
7.4. Symmetries and Orderings in Multiferroics193
7.5. Theory of Magnetoelectric Coupling in Multiferroics194
7.6. Magnetoelectric Multiferroics201
Acknowledgements219
References219
8. Electronic Correlations and Metal-Insulator Transitions224
8.1. Introduction: The Meaning of Localization – Delocalization Transitions in Solids with Examples224
8.1.1. Crystallization of Liquid 3He as Mott-Hubbard Transition224
8.1.2. Localization-Delocalization Transition of Ultracold Atoms226
8.1.3. Metal-Insulator Transition in Doped V2O3227
8.2. Elementary Approach to the Metal-Insulator (Mott-Hubbard) Transitions229
8.2.1. Normal metal as a Landau Fermi liquid: basic characteristics229
8.2.2. Mott-Wigner Criterion of Localization231
8.2.3. 8.2.3 Localization on the Lattice: Hubbard Model233
8.2.4. Quantitative Discussion of the Metal-Insulator Transition234
8.2.5. Quasiparticle Representation of Correlated-Electron System and the Phase Diagram237
8.2.6. Mott-Hubbard Localization in Correlated Nanoscopic Systems242
Acknowledgment245
References245
8.3. Concluding Remarks245
9. Nature of the Insulator-Metal Transition in Transition Metal Oxides Induced by Chemical Defects – Deviation from Stoichiometry and Electrochemical Alkaline Intercalation 246
9.1. Insulator-Metal Transition in Transition Metal Oxides Induced by Deviation from Stoichiometry248
9.2. Insulator-Metal Transition in Transition Metal Oxides Induced by Electrochemical Alkaline Intercalation/Deintercalation273
9.2.1. LixCoO2277
9.2.2. NaxCoO2-y286
Acknowledgements296
References297
10. Structural Transformation of the SrTiO3 Surface Region due to Electric Fields at Ambient Temperature 300
10.1. Modifications and Equilibrium of the SrTiO3 Structure301
10.1.1. Compositional Changes: the Quasi-binary System SrO–TiO2301
10.1.2. Stability of SrO(SrTiO3)n Ruddlesden-Popper Phases304
10.1.3. A Look at Symmetry and Property Tensors305
10.1.4. Chemical Modifications Beyond the Ternary Composition307
10.2. Electric-field Induced Ionic Transport and Anisotropy in SrTiO3308
10.2.1. Electroformation309
10.2.2. Redistribution of Ionic Species311
10.3. Evidence for Structural Transformations and Related Models313
10.3.1. Structural Transitions due to Application of an Electric Field313
10.3.2. The Occurence of Ruddlesden-Popper Phases314
10.3.3. The Migration-Induced Field-Stabilized Polar (MFP) Phase315
10.4. Modification of SrTiO3 Properties and Related Applications318
10.4.1. Oxygen Vacancies and Conductivity319
10.4.2. Mechanical Properties320
10.4.3. Magnetism322
10.4.4. Pyroelectricity322
10.4.5. Piezoelectricity324
10.4.6. Resistive Switching326
10.4.7. All-Solid-State All-in-One Battery327
10.4.8. Further Applications327
10.5. Conclusion328
Acknowledgment329
References330
11. Chemical Transformation of SrTiO3 Surface Region Exposed to High Temperature and Other Factors 337
11.1. Introduction337
11.2. Investigated Crystals340
11.3. Possible Surface Reconstructions of STO341
11.4. Methods of Surface Studies342
11.5. Thermal Treatment342
11.6. Surface Modification upon Vacuum and Exposure to X-Rays and Electron Beam349
11.7. Ion Sputtering352
11.8. Deposition of Metals355
11.9. Mechanical Stress and Defects356
Summary357
References358
12. Chemical Transformation of TiO2 Surface Region Exposed to High Temperature and Different Chemical Activity of Oxygen360
Acknowledgements376
References376
13. From Electroformation to Resistive Switching in Single Crystals of Strontium Titanate: How SrTiO3 Can Be Transformed into a Metallic State Using Electrical Stimuli 379
13.1. Introduction379
13.2. Resistive Switching – General Information382
13.3. Some Theoretical Considerations387
13.3.1. Methods for the Calculation of the Electronic Structure389
13.3.2. Trends Observed from DFT Calculations394
13.4. Electroforming of Non-conducting (Insulating) SrTiO3 Crystals395
13.4.1. Electrical Characterization During Electroformation395
13.4.2. Oxygen Evolution During Electroformation400
13.4.3. Spatial Inhomogeneity of the Electroformation Process and Filamentary Structures403
13.5. Model411
References418
14. Crystallographic Structure, Electronic Structure, and Chemical Composition on the Nanoscale: Important Role of the SPM, LEED, Photoemission Investigations for the Analysis of the Crystal Geometry, Electronic Structure and Diffusion Phenomena on the Surface of Model Oxides 421
Acknowledgements438
References438
15. Investigations of Local Thermal Properties by SThM Microscopy440
15.1. Scanning Thermal Microscopy: Principle, Equipment, Operation Modes441
15.2. Thermal Imaging: Temperature and Conductivity Contrast Measurements446
15.3. Quantitative Thermal Measurements with SThM Equipment – Potentialities and Limitations449
15.4. Methods for Improvements of Sensitivity and Stability of Thermal Measurements Using Batch Fabricated Thermal Probes454
15.5. Determination of the Thermal Conductivity of Submicron Layers on Thick Substrates459
15.6. Application of Qualitative and Quantitative SThM Measurements in Investigation of Perovskites (Thin Films, Bicrystals)461
Acknowledgements463
References464
16. Studying the Local Redox Processes on Transition Metal Oxides Surfaces Using Kelvin Probe Force Microscopy467
16.1. Introduction467
16.2. Principles of Kelvin Probe Force Microscopy469
16.2.1. Basics of KPFM Operation469
16.2.2. Forces in Atomic Force Microscopy470
16.2.3. Technical Realization of KPFM473
16.2.4. Limits of Resolutions in KPFM475
16.3. Local Surface Potential of Oxide Metal Surfaces upon Reduction and Oxidation Processes479
16.3.1. Titanium Dioxide TiO2(110) Surface479
16.3.2. Strontium Titanate SrTiO3(100) Surface485
16.4. Summary492
Acknowledgements493
References493

2.4.TypicalMethodsforEvaluationofQualityofOxideCrystals

theintensityofthebeam,butenhancethedepthofﬁeldofthespecimen

anddepthoffocusoftheimages[79].ThemostseriouslimitationofTEM

isthenecessityofinvestigationofthinspecimens,preferablythinnerthan

100nm.Theappropriateproceduresforthepreparationofadequatelythin

sampleshavebeenproposedforalmostalltypesofmaterials.Usually,

TEMprovidestheinformationonthemeansizeandshapeoftheperovskite

nanoparticlesandtheirnumber[64,73,83].

TEMandnumerousmodiﬁcationsofthistechniquepermitanalysis

ofdiferentsignalsgeneratedwhenahigh-energybeamofelectronsinter-

actswithathinspecimen,i.e.thesignalsfromthebeamsreﬂectedatdif-

ferentanglesfromthesurface(Augerelectrons,backscatteredelectrons,

secondaryelectrons,characteristicX-rayorvisiblelight)aswellasthose

passingthroughthesample(elasticallyscatteredelectrons,inelastically

scatteredelectrons,bremsstrahlungX-rays).Whenthesampletobestudied

isofabout10nminthickness,ahigh-resolutionTEM(HRTEM)canbe

applied.Thismethodofersahighlyaccuratetransformationofthesample

structuredetailsfromthespecimentotheimage.Thistransferischarged

withtwomainproblems,theﬁrstisthattheopticalsystemisnotperfect

andthelenseshaveaﬁnitesize(Abbe’stheory),whilethesecondisrelated

tothedimcultiesinapplicationoftheatomisticmodelforinterpretation

oftheimage.

Transformationofthesamplefeaturesintothebestpossibleimageby

anelectronmicroscoperequirescorrectuseofanumberofproceduresthat

couldbedescribedinthefollowingway:theopticalsystemtransforms

acertainpointf(x,y)inanextendedregionintheimageg(x,y),preferably

intheformofacirculardisk,todescribethisprocessthepoint-spread

functionh(r)isintroducedandtheprocessoftransformationiscalledthe

convolutionoff(r)withh(r).Ofcourse,fortwoclose-lyingpointsinthe

sample,theimagewillhaveacommonpartobtainedasaresultoftheover-

lappingofthetwocirculardiskscorrespondingtothesepoints.Inorderto

getahighresolution,itisnecessarytoprovidehighspatialfrequencies,

whichcorrespondstoverysmallworkingdistances.

Eachpointoftheimagehasacharacteristicintensitywhichfortwo-di-

mensionscanbepresentedasasumoftwosinusfunctionsandthisindi-

catesapossibilityofFouriertransformapplication.Thistransformation

musttakeintoaccountthecontributionsduetotheapertures,attenuation

ofthewave,andaberrationofthelensthroughtheintroductionofappropri-

atefunctionssothattoobtainalinearrelationshipbetweentheimageand

theweakspecimenpotential.Forverythinsamples,theelectronspassing

throughthesampleundergoaphaseshiftthatpermitstheapproximation

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