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The article contains sections titled: 1. Introduction 2. Theoretical Background 2.1. Dielectric Effects and Classification of Dielectrics 2.2. Characteristic Dielectric Parameters 3. Linear Dielectrics 3.1. Al 2 O 3 3.2. New Substrate Materials 3.3. Polymer–Ceramic Composites 4. Nonlinear Dielectrics 4.1. Physics of Ferro‐ and Piezoelectricity 4.2. BaTiO 3 (BT) 4.3. PbTiO 3 , PbZrO 3 , PbTiO 3 –PbZrO 3 4.3.1. Crystal Structures, Processing, and Properties 4.3.2. Applications 4.4. PLZT 4.5. Pb(Mg 1/3 Nb 2/3 )O 3 /Pb(Zn 1/3 Nb 2/3 )O 3 (PMN/PZN) 4.6. PbNb 2 O 6 4.7. LiNbO 3 , LiTaO 3 4.8. Lead‐Free Perovskites 4.9. Calcium Gallium Germanate (CGG) Compounds 4.10. Other Materials 5. Semiconducting Ceramics 5.1. SiC 5.1.1. Structure and Properties 5.1.2. Single‐Crystal Growth 5.1.3. Doping and Device Fabrication 5.1.4. Applications 5.2. TiO 2 6. Superconducting Ceramics 7. Sensor Materials 7.1. Oxide‐Based Sensors 7.2. Ferroic, Smart, and Intelligent Sensors
The article contains sections titled: 1. Introduction 2. Theoretical Background 2.1. Dielectric Effects and Classification of Dielectrics 2.2. Characteristic Dielectric Parameters 3. Linear Dielectrics 3.1. Al 2 O 3 3.2. New Substrate Materials 3.3. Polymer–Ceramic Composites 4. Nonlinear Dielectrics 4.1. Physics of Ferro‐ and Piezoelectricity 4.2. BaTiO 3 (BT) 4.3. PbTiO 3 , PbZrO 3 , PbTiO 3 –PbZrO 3 4.3.1. Crystal Structures, Processing, and Properties 4.3.2. Applications 4.4. PLZT 4.5. Pb(Mg 1/3 Nb 2/3 )O 3 /Pb(Zn 1/3 Nb 2/3 )O 3 (PMN/PZN) 4.6. PbNb 2 O 6 4.7. LiNbO 3 , LiTaO 3 4.8. Lead‐Free Perovskites 4.9. Calcium Gallium Germanate (CGG) Compounds 4.10. Other Materials 5. Semiconducting Ceramics 5.1. SiC 5.1.1. Structure and Properties 5.1.2. Single‐Crystal Growth 5.1.3. Doping and Device Fabrication 5.1.4. Applications 5.2. TiO 2 6. Superconducting Ceramics 7. Sensor Materials 7.1. Oxide‐Based Sensors 7.2. Ferroic, Smart, and Intelligent Sensors
The effects of Mg doping (Mg Al ) and native N vacancy (V N ) on the electronic structures and transport properties of AlN nanowire (AlNNW) were theoretically investigated by using density functional theory. Either the Mg Al defect or the V N defect prefers to be formed on the AlNNW surfaces. Both Mg Al and V N defects could increase the conductivity owing to introducing a defect band inside the band gap of AlN and split the AlN band gap into two subgaps. The defect concentration has little influence on the magnitude of the subgaps. The Mg Al serves as a shallow acceptor rendering the nanowire a p-type conductor. The V N introduces a deep donor state enabling the nanowire an n-type conductor. The Mg Al systems exhibit higher conductivity than the V N ones owing to the narrow subgaps of Mg Al systems. The conductivity is roughly proportional to the defect concentration in the Mg Al and V N defect systems. When the Mg Al and V N coexist, the hole state of the Mg Al defect and the electron state of the V N defect will compensate each other and their coupling state appears just above the valence-band maximum leading to a little decrease of the band gap compared with the pure AlNNW, which is unfavorable for the enhancing of the conductivity.N vacancy, Mg doping, electronic property, transport property, AlN nanowire Citation:Qin M, Shang Y, Zhang G L. Mg doping and native N vacancy effect on electronic and transport properties of AlN nanowires.
The growth of aluminum nitride thin films onto various substrates (glass, flexible polyimide, or silicon) and onto different buffer layers (Au, Nb, Cu, Ag, Co, Fe, NiFe, or IrMn) is reported. Samples grown on IrMn, Co, NiFe, Nb, or Au show smooth surfaces. This same smooth quality is observed in samples grown at a lower 200 °C temperature directly on glass, Si, or flexible polyimide. In applications where thin and smooth piezoelectric films are necessary, c‐axis‐oriented AlN can be grown onto a wide range of different surfaces: conducting, insulating, ferromagnetic, antiferromagnetic, or flexible. Copyright © 2014 John Wiley & Sons, Ltd.
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