Designing Nanoscale Materials Lecture Series by 2004 Debye Institute Professor Christopher B. Murray IBM Research Ornstein Laboratory 166 Office phone 253 2227 cbmurray@alum.mit.edu Debye Lecture 6 Nanostructured Magnetic Materials for Information Technology C. B. Murray Magnetic Nanocrystals and Nanocrystal Superlattices Inorganic C.B. Murray, S. Sun, F. X. Redl, K. S. Cho and W. Gaschler. Core 1-15nm IBM T. J. Watson Research Center; Yorktown Heights, NY (1) Synthesize, characterize and integrate nanostructured materials. (2) Probe the limits conventional materials/device scaling. (3) Harness mesoscopic properties for future technology. Surfactants (4) 1-4 nm thick Film Growth: Self-Assembly Explore the potential of self-assembly for nanofabrication. Nanocrystal Superlattice A Synthesis B 250C Annealed Superlattice 60 nm Reagents 30 nm C Size Selective Processing D 80 nm 5 nm Patterning & addressing Applications & Opportunities for High Energy Product magnets. Automotive and Avionic Components Micro/Nano Devices Medical diagnostic system Various actuators Hard disk drives in acoustic systems Head actuators •Single magnetic domain particles. M (emu) Superparamagnetism 5K 300K •Orientation determined by anisotropy energy, K. 0.02 •Energy barrier, ∆E = KV / k BT •Remnant magnetization, M rem M rem (t ) = M sat e −t / τ 0.04 0.00 where τ = τo e − KV / k T •Blocking temperature, k BTB ≈ 25∆E B -4000 -2000 0 2000 H (G) 4000 -0.02 •At T >> TB , particles are superparamagnetic. -0.04 •Zero hysterises – Langevin equation • M ( H ) = coth(µH / k BT ) − k BT / µH 8nm MT Co 90 K 120 K 150 K 180 K 210 K 240 K 270 K M (emu) Energy •At T << TB , particles are ferromagnetic. 0.04 0.02 ∆E 0.00 -100 -50 0 -0.02 Orientation -0.04 50 100 H/T (G/K) 8.00E-02 2.50E-03 6.00E-02 1.88E-03 Magnetic Moment (Emu) Magnetic Moment (Emu) Magnetization - size dependence 4.00E-02 2.00E-02 0.00E+00 -2.00E-02 -4.00E-02 6.25E-04 0.00E+00 -6.25E-04 -1.25E-03 -1.88E-03 -6.00E-02 -8.00E-02 -5000 1.25E-03 -3000 -1000 1000 3000 Magnetic Field (Gauss) dipole interaction no dipole interactions 10nm fcc-Co particles 5000 -2.50E-03 -5000 -3000 -1000 1000 3000 Magnetic Field (Gauss) dipole interactions no dipole interactions 2-2.5nm fcc-Co particles 50 Synthesis and Self-assembly of Co nanoparticles • • • High temperature (200 oC), solution phase synthesis. Rapid nucleation – growth controlled by coordinating ligands. Size distribution improved by size selective precipitation. Film Growth :Self-Assembly Nanoparticle Superlattice Size selective precipitation Annealed Superlattice Synthesis of Transition Metal Nanocrystals Co2+ + (Et)3BH + R3P + C17H19COOH 250C Na+Napth- Sequential reduction of metals Core/Shell Mn+ Co2+ + C16(OH)2+R3P + C17H19COOH Simultaneous reduction of metals alloys Co2(CO)8 + R3P + C17H19C00H CoM Co2+ + Mn+ AA 60 nm Co 8 nm Ni 9 nm Co/Ni 9 nm FePt 4 nm Crystal phases of Cobalt 3 crystal phases are studied.. Fcc and hcp differ only in stacking sequence of close-packed layers. fcc: ABCABC… Hcp: ABABAB... A B A (1) hcp Co C B A (2) fcc Co •Cubic unit cell •Complex internal structure Set I - 8 atoms Set II - 12 atoms (3) ε-Co Dinega, D.P; Bawendi, M.G. Angew. Chem., 1999, 38(12), 1788. XRD modeling of cobalt nanoparticles Better fits obtained by including – – • • Stacking faults Twin faults Introduction of stacking faults generates mixed fcc/hcp structures. Leads to the inter conversion of fcc and hcp phases A A A A B B B B C C C fcc 75% fcc Intensity • 50% fcc 75% hcp Twin Plane A A A B B B B C C C C Stacking Fault hcp 30 40 50 60 70 2θ 80 90 100 002 XRD Modeling of hcp nanoparticles 101 Intensity 4nm 6nm 8nm 50 2θ 60 70 110 40 100 Intensity 10nm Expt. Fit 35 nm • • 40 50 60 70 2θ TEM images show that hcp Co nanoparticles are slightly prolate. XRD fitting show extensive faulting/disorder. – – Approximately one fault every 2.5 stacking planes. Consistent across a variety of particle sizes. 80 90 40 50 60 311 70 2θ 50 80 55 2θ 60 Expt Fit 90 65 100 520 45 510 40 420 330 321 211 Intensity 310 Intensity (arbitrary units) 221 3nm 5nm 7nm 9nm 70 111 XRD Modeling of fcc nanoparticles Intensity 4nm 7nm 8nm 200 40 40 50 60 50 Expt. Fit 70 80 2θ 60 90 2θ • • TEM images show that fcc Co nanoparticles are spherical in shape. XRD fitting - one fault every 4 planes. – • 70 220 Intensity 20 nm 6nm Bad fits at higher angles. Dark regions in TEM imply “multiple twinned” (MT) structures. 100 111 6nm Intensity Intensity (arbitrary units) 4nm 7nm 40 45 50 Expt. Fit 40 50 60 70 2θ 80 55 2θ 60 65 70 220 200 8nm 90 100 XRD Modeling of MT polyhedra • Better fits have been reported for MT polyhedra – – • Highly faceted structures Icosahedral, cubeoctahedral and decahedral structures suggested HR-TEM images also suggest the presence of multiple domains – Consistent with multiple twinning Decahedron 2.0 nm Cubeoctahedron Icosahedron Hall,B.D. et al., Phys. Rev. B, 1991, 43(5), 3906. 221 XRD Modeling of ε-Co nanoparticles 310 Intensity 3nm 5nm 7nm 50 60 2θ 70 70 420 510 Expt Fit 60 80 90 520 50 330 211 40 40 321 311 Intensity 9nm 100 2θ • • • TEM images show that ε-Co forms as spherical nanoparticles with narrow size distributions. XRD fits - perfect crystalline internal structure. Supported by HR-TEM images of individual nanoparticles. Modeling of the magnetization of Co nanoparticles •Equilibrium partition function of nanoparticles in applied magnetic field. ρ ρ − E ( Hρ , µρ,K ,V ) / k T ∫ dµθ ∫ dµϕ M sat ( µ • Hρ )e < M >= ∫ dKp ( K ) ∫ dVp (V ) ∫ dH θ ∫ dH ϕ ρ − E ( H , µ , K ,V ) / k T dµ dµ e ∫ θ∫ ϕ ρ ρ E / V = − M sat µ • H − KS z2 B B M rem (t ) = ∫ dKp ( K ) ∫ dVp (V )[αM sat e −t / τ ] where τ = τ o e − KV / k T B Moment, µ θ Easy axis Applied Field Magnetic modeling of MT Co nanoparticles M (emu) 0.06 Saturation Magnetization (1 Tesla) 0.05 0.06 0.04 M (emu) 0.04 Expt. Fit 0.02 0.03 For 0.1 T, only T>170 K in equilibrium 0.00 -10000 0.02 -5000 0 5000 -0.02 0.01 Remnant Magnetization (120 s) -0.04 0.00 0 50 100 150 200 250 300 -0.06 T (K) • • TEM analysis - 7 nm diameter Magnetic fitting – – • • • Diameter K 6.2 + 0.5 nm 7.0x105 + 3.5x105 ergs cm-3 Smaller “magnetic” diameter accounted for by the presence of oxide layer. Anisotropy close to bulk fcc value Remnant magnetization is half saturation magnetization at low temperatures – Implies uniaxial symmetry. 10000 H (G) Magnetic modeling of MT Co nanoparticles M (emu) 0.06 Saturation Magnetization (1 Tesla) 0.05 0.06 0.04 M (emu) 0.04 Expt. Fit 0.02 0.03 For 0.1 T, only T>170 K in equilibrium 0.00 -10000 0.02 -5000 0 5000 -0.02 0.01 Remnant Magnetization (120 s) -0.04 0.00 0 50 100 150 200 250 300 -0.06 T (K) TEM analysis - 7 nm diameter Magnetic fitting Diameter 6.2 + 0.5 nm K 7.0x105 + 3.5x105 ergs cm-3 Smaller “magnetic” diameter accounted for by the presence of oxide layer. Anisotropy close to bulk fcc value Remnant magnetization is half saturation magnetization at low temperatures Implies uniaxial symmetry Predicted for MT polyhedra 10000 H (G) Magnetic modeling of ε-Co nanoparticles 0.004 M (emu) Saturation Magnetization (1 Tesla) 0.003 M (emu) (0.1 Tesla) 0.004 0.002 Expt. Fit 0.002 0.000 -10000 0.001 Remnant magnetization (120 s) -5000 0 5000 -0.002 0.000 0 50 100 150 200 250 300 -0.004 T (K) • • TEM analysis - diameter of 9.5 nm Magnetic fitting – – • • Diameter 8.4 + 0.9 nm Anisotropy 7.1x105 + 4.0x105 ergs cm-3 Anisotropy also close to bulk fcc value Remnant magnetization is half saturation magnetization at low temperatures – Implies uniaxial symmetry. 10000 H (G) Materials Selection: KuV >> kT Ku 103 Ni NiO.Fe2O3 Fe 104 105 106 107 108 109 Cubic KuV >> kT KuV < kT CoOFe2O3 BaO.6Fe2O3 Co MnAl CoPt FePt Fe14Nd2B YCo5 SmCo5 SmFe11Ti Hexagonal Tetragonal Hard magnets Crystal Anisotropy Shape Anisotropy Exchange Anisotropy Strain Anisotropy Co Pt CoPt L10 structure (tetragonal) Shape ? Solution phase synthesis Example: FePt nanopartilces Starting Materials Mixing Particle dispersion FeCl2 FePt FePt FePt Pt(acac)2 FePt FePt COOH (acid) FePt FePt FePt NH2 (amine) FePt LiBEt3H (Superhydride ) 200-260°C H 3C CH 3 O O Pt(acac)2 = Pt O H 3C O CH 3 S. Sun, C. B. Murray, IBM Yorktown Nanoparticles for magnetic storage • Narrow size distribution higher thermal stability • Smaller particles narrower transition widths 35 GBit/in2 prototype media 8.5 nm grains σarea ≅ 0.6 50 nm Nanoparticle arrays 4 nm FePt particles σarea ≅ 0.05 50 nm S. Sun, Ch.Murray, D. Weller, L. Folks, A. Moser, Science, 287 (2000) 1989 Magnetic properties • Annealing leads to formation of ordered, ferromagnetic phase Chemically disordered fcc structure Superparamagnetic Annealing at 550C Pt Chemically ordered fct structure Ferromagnetic Fe C axis Magnetic properties • Order parameter and coercivity increase with annealing temperature and duration 3 layer samples of 6 nm FePt particles 1 0 -100 -200 580 ºC 650 ºC 400 ºC 450 ºC -300 -20-15-10 -5 0 5 10 15 20 H (kOe) Order parameter 200 100 20 0.8 N2 0.6 15 N2 10 0.4 FG 5 0.2 FG 0 0 30 0 40 0 500 60 0 700 80 0 90 0 tempe ratu re (C ) XRD data M. Toney, IBM Almaden Hc (kOe) M (emu/cm3) 300 VSM Hysteresis loops 3 layers, annealed in N2 at 580 C for 30 min, FePt samples from FeCl2 0.15 perpendicular parallel moment (memu) 0.1 “3D” random assembly of 4nm particles 0.05 0 -0.05 -0.1 -0.15 -20 -15 -10 -5 0 5 10 magnetic field (kOe) 15 20 Chemical analysis 12 20% Fe 80% γ Fe2O3 8 4 Unannealed Hc = 0 0 700 705 710 715 720 725 730 energy (eV) Total electron yield (rel. units) Total electron yield (rel. units) • Near Edge X-ray Absorption Fine Structure (NEXAFS) spectroscopy shows iron oxide fraction that is reduced upon annealing • NEXAFS more sensitive to particle surface - averaged ratio may be 16 16 different 12 60% Fe 40% γ Fe2O3 8 4 650 oC 5 min, Hc = 8.4 kOe 0 700 705 710 715 720 725 730 energy (eV) Special thanks to Robin Farrow for providing iron oxide reference samples. Structural properties a c b 50 nm 1 20 0.8 15 0.6 10 0.4 5 0.2 0 0 0 400 800 o 50 nm (111) coherence length (nm) Fraction of L10 pahse 50 nm TEM images of 6 nm particles (a) as synthesized (b) 530 ºC for 60 min in vacuum (c) 600 ºC for 60 min in vacuum TEM images courtesy of Zu-Rong Dai • X-ray scattering and TEM used to study structural properties 3 layers of 4 nm particles annealed in N2 tem perature ( C) XRD data M. Toney, IBM Almaden Polymer-mediated self assembly • Substrate surface is functionalized • Dipped into dispersion of stabilized nanoparticles • Ligand exchange leads to formation of strongly bound layer of nanoparticles • New layer of functional molecule replaces stabilizer Substrate • Repeat process to form multilayers Substrate Functional polymer Substrate Substrate S. Sun, C. B. Murray, IBM Yorktown Magnetic recording Computer V Servo Electronics I 4 nm ferromagnetic FePt particle assembly Writing > Slider Sample > X-Y Piezo Scanning Stage to piezos Reading 500 fc/mm 4 2 0 1040 fc/mm MR signal [mV] -2 -4 -6 2140 fc/mm -8 -1 0 5000 fc/mm -1 2 -1 4 -1 6 -1 8 -2 0 0 5 10 15 x [µ m ] 20 25 Size control of nanocrystals in the absence of Ostwald ripening p r e c u r s o r s nucleation growth Factors influencing the nucleation rate fast until all monomer is consumed slow CoPt3 nanocrystals 220 oC 170 oC 200 oC 145 oC • reaction temperature • concentrations of precursors • concentrations of surfactants Fe2O3 nanocrystals 307 oC 255 oC 245 oC 200 oC Cobalt Nanocrystal Superlattices (T. Betley et al) Hexagonal packing Cubic packing 10 nm Cobalt NCs Three-dimensional colloidal supercrystals of CoPt3 nanocrystals Institute of Physical Chemistry, University of Hamburg, Hamburg, Germany hν hν vacuum secondary electrons sample surface Electron escape depth 5 nm Photon penetration depth 50 nm sample FePt Fe2O3 polymer 3 2.5 2 FePt 1.5 Fe2O3 1 ) 10 -6 0.5 Magnetisation (emu x10 contribution to spectrum (rel. units) For the unannealed particles the ratio in the spectra can be estimated as 20%Fe, 80% Fe2O3 (I am still not sure what oxide we have, maybe a mixture). On the left is the contribution to the spectra as a function of radius. A 3nm diameter FePt metal core with a 0.5nm thick oxide shell would produce such a spectrum. 0 0 0.5 1 1.5 2 2.5 radius (nm) 20% Fe 80% gammaFe2O3 5 FePt 100201A-2 Perp2 Unannealed Hc = 258 Oe S = 0.10 0 -5 100201-A2 -10 14 -15 -10 12 -5 0 5 Applied Field (kOe) 10 15 10 15 10 10 Magnetisation (emu x10 -6 ) 8 6 4 2 0 700 5 FePt 100201A-2 Inplane Unannealed Hc = 242 Oe S = 0.14 0 -5 -10 705 710 715 720 725 730 735 -15 energy (eV) -10 -5 0 5 Applied Field (kOe) 2 1.5 FePt Fe2O3 1 For the annealed particles the metal ratio is much higher, here an example for 650C/5min anneal. On the left is the contribution to the spectra as a function of radius. A 3.6 nm diameter FePt metal core with a 0.2nm thick oxide shell would produce such a spectrum. 0.5 0 0.5 1 1.5 2 2.5 ) 0 100 Magnetisation (emu x10 -6 contribution to spectrum (rel. units) 2.5 radius (nm) 101701C 60% Fe 40% gammaFe2O3 FePt 101701C Perp2 Annealed 650/5 SS Hc = 7847 Oe S = 0.77 50 0 -50 -100 12 -10 10 100 -6 ) 8 Magnetisation (emu x10 6 4 2 0 Applied Field (kOe) 10 FePt 101701C Inplane Annealed 650/5 SS Hc = 7115 Oe S = 0.76 50 0 -50 -100 0 695 700 705 710 715 energy (eV) 720 725 730 735 -10 0 Applied Field (kOe) 10 FePt gamm aF e2O3 F e3 O4 alpha F e2O3 FePt gamm aF e2O3 F e3 O4 alpha F e2O3 0.7 2.5 (2) 0.6 2 (3) 0.5 1.5 (1) 0.4 1 (1) 0.3 0.5 0.2 0 718 0.1 720 7 22 724 ene rgy (eV) L3 726 728 730 734 735 736 7 37 738 ene rgy (eV) L2 739 740 741 742 lef t norm right norm F e3O 4 ru n 2012513 F e3O 4 ru n 2012513 0.2 6 0 5 -0.2 4 -0.4 3 -0.6 -0.8 2 -1 1 -1.2 0 715 720 725 730 735 740 -1.4 745 715 720 7 25 730 735 7 40 745 energy (e V) ene rgy (e V) Polar Kerr H Fe3O4 0.1 Kerr signal Fe3O4 sample from Robin XMCD in 500 Oe, 20 degrees incidence along easy axis run 20125013 0.05 0 -1000 -500 0 -0.05 -0.1 field (Oe) 500 1000 201240_20su m Fe3O4 Rob in run 20124021 0.2 0.4 0 0.2 0 -0.2 -0.2 -0.4 -0.4 -0.6 -0.6 -0.8 -0.8 -1 -1 -1.2 -1.2 715 720 7 25 730 735 7 40 745 ene rgy (e V) Fe3O4 sample from Robin XMCD in 500 Oe, 20 degrees incidence along easy axis test reproducibility - is very good 715 720 7 25 730 ene rgy (e V) 735 7 40 745 Three layers of PEI-E066 on Si(110) annealed under Ar + H(5%) for 30 min. The samples have been immersed into acetone for 1 min and dried. 030902-A, 400C 030902-B, 450C 030902-C, 500C 030902-D, 530C 030902-E, 560C 030902-F, 580C 030902-A 400C Hc=0 Ms=115 emu/cm^3 400 M (emu/cm^3) 300 200 100 0 -20 030902-C 500C Hc=2.28 Ms=305 emu/cm^3 300 200 200 0 -200 20 M (emu/cm^3) M (emu/cm^3) 300 10 100 0 -20 -10 -100 0 -200 -300 -300 -400 -400 H (kOe) 20 H (kOe) 400 0 10 -400 400 -100 0 -300 100 -10 -100 -200 030902-B 450C Hc=0.77 Ms=312 emu/cm^3 -20 -10 H (kOe) 10 20 And here the comparison between 8nm, 6nm, and 4nm. 0.06 4nm 5L 6 nm 7L 0.05 8nm 7L 0.04 0.03 0.02 0.01 0 700 705 710 7 15 720 en ergy (eV) 7 25 730 735 740 030902-E 560C Hc=2.7 kOe Ms=319 emu/cm^3 400 400 300 300 200 200 100 0 -20 -10 -100 0 10 20 -200 M (emu/cm^3) M (emu/cm^3) 030902-D 530C Hc=2.3 kOe Ms=380 emu/cm^3 100 0 -20 -10 -100 0 10 20 -200 -300 -300 -400 -400 H (kOe) H (kOe) 5 030902-F 580C Hc=4.8 kOe Ms=316 emu/cm^3 350 Ms 400 4 300 3 250 M (emu/cm^3) 300 200 100 Hc 0 -20 -10 -100 0 10 20 2 200 1 150 -200 -300 -400 H (kOe) 0 350 400 450 500 550 Anneal temperature (C) 100 600 0.5 0.4 0.3 0.2 0.1 0 350 400 450 500 550 Anneal temperature (°C) From Mike Toney, XRD 600 12 10 8 6 4 2 0 350 400 450 500 550 Annealing temperature (°C) From Mike Toney, XRD 600 30 B Total electron yield (rel. units) 25 A C D 20 α− Fe O 2 γ − Fe O 15 2 Fe O 3 10 400°C 450°C 500°C 530°C 560°C 580°C 5 0 700 4 705 710 715 720 energy (eV) 725 Fe 730 3 3 Hello, Here the data from the latest ALS run. Jan made two samples for comparison, sample #4 is 50 nm Fe55Pt45 without cap layer sample #5 is 50 nm Fe55Pt45 with 2 nm Pt cap layer Here the Fe spectra for comparison. The one without cap layer is much more oxidized as expected. total yield (rel. units) sample #4 FePt no cap sample # 5 FePt with cap 5 4.5 4 3.5 3 2.5 2 1.5 1 0.5 0 700 4 5 710 720 730 energy (eV) 740 750 This graph shows sample #5 with respect to a clean Fe reference, and the best fit to the spectrum I got with assuming 70% Fe and 30% FeO. 0.05 Fe 70%F e30% FeO #5 0.04 0.03 0.02 0.01 0 700 705 710 715 720 energ y (eV) 7 25 730 735 740 And the contribution to the spectra of Fe and Fe3O4 for 8nm, 6nm, and 4nm. If I put this into the model the oxide layer for the 6 and 8 nm particles seems to be thinner (2A) than for the 4 nm particles (4A). Fe f raction (% ) Fe3 O4 fra ction (% ) 80 70 60 50 40 30 20 3 4 5 6 pa rticle size (nm) 7 8 9 -20 -10 0.12 0.1 0.08 0.06 0.04 0.02 0 -0.02 0 -0.04 -0.06 -0.08 -0.1 041801-F Hc=10.8 kOe 0.15 10 20 Polar Kerr angle (deg) Polar Kerr angle (deg) 041801-E Hc=2.35 kOe 0.1 0.05 0 -20 -10 -0.05 0 10 -0.1 -0.15 H (kOe) H (kOe) 6nm 8nm The 8nm sample has very high coercivity. 041801-E E098, 6nm Fe52Pt48 SiO2/Si PEI-E098, 7Layers N2, 580C, 30 min 041801-F E095, 8 nm ~Fe52Pt48 SiO2/Si PEI-E095, 7Layers N2, 580C, 30 min 20 This is a comparison of the films made 030101. They are all just after the onset of being ferromagnetic, the spectra are all very similar. 4nm 3L F e50 Pt50 F e(C O)5 4nm 3L F e55 Pt45 F e(C O)5 8nm 1 L FeC l2 4nm 2 L Fe5 8Pt4 2 FeC l2 4nm 2 L Fe5 8Pt4 2 FeC l2 2.5 2 1.5 1 0.5 0 700 705 710 7 15 720 en ergy (eV) 725 730 735 740 030101-A Hc=1.2 kOe 0.01 0.005 0 -20 -10 -0.005 0 10 20 -0.01 -0.015 Polar Kerr angle (deg) Polar Kerr angle (deg) 0.02 0.015 -20 -10 -0.02 H (kOe) 0.01 0.005 0 10 20 -0.01 -0.015 Polar Kerr angle (deg) Polar Kerr angle (deg) 0.02 -0.005 0 20 -20 -10 0.01 0.008 0.006 0.004 0.002 0 -0.002 0 -0.004 -0.006 -0.008 -0.01 H (kOe) 030101-D Hc=1.2 kOe 0.015 -10 10 H (kOe) 030101-B Hc=2.4 kOe -20 0.025 0.02 0.015 0.01 0.005 0 -0.005 0 -0.01 -0.015 -0.02 -0.025 Hc=1.1 kOe Polar Kerr angle (deg) 030101-C Hc=0.14 kOe -20 -0.02 H (kOe) -10 0.025 0.02 0.015 0.01 0.005 0 -0.005 0 -0.01 -0.015 -0.02 -0.025 10 20 H (kOe) 030101-A E066, Fe58Pt42 SiO2/Si PEI-Fe58Pt42, 2 layer N2, 580C, 30 min 030101-B E066, Fe58Pt42 SiO2/Si PEI-Fe58Pt42, 2 layer N2, 580C, 30 min 030101-C F062, Fe50Pt50 SiO2/Si PEI-Fe50Pt50, 3 layers N2, 580C, 30 min 030101-D F070, Fe55Pt45 SiO2/Si PEI-Fe55Pt45, 3 layers N2, 580C, 30 min 030101-E E068, ~8nm FePt SiO2/Si PEI-FePt, 1 layer N2, 580C, 30 min 10 20 Hi all, I did a calculation of the signal one would expect in total yield detection for the following geometry: This is basically a particle of 40A diameter with 32A FePt core surrounded by one monolayer Fe3O4. It is embedded in the polymer (for the calculation I assumed just carbon) with 60A particle distance, that gives about 10A carbon on top. polymer Fe3O4 FePt 32A 40A 10A Fe3O4 Nanocrystals (Sun and Zeng) Fe(acac)2 or Fe(acac)3 TOE or DOE OA (and tributylphosphine) 300 C TOA or DOE OA, 350 C armorphous Fe-NC Fe(CO)5 TOA, OA 300 C N O Ox in air FeO >300 C Fe + Fe3O4 Shape selective synthesis of wuestite Substitute trimetylamine N-oxide with pyridin N-oxide Fe(CO)5 oleic acid dioctyl ether or trioctylamine ∆T FeO-NC N O FeO Nanoparticles Right a) TEM image of a single cubic superlattice built of cubic FeO nanocrystals with 11 nm edge length. b) TEM image of a larger superlattice oxidized or decomposed after storage. c) SAED of the cubic superlattice in b) showing reflections for magnetite and orientational ordering in the superlattice. Right: a) LRTEM image of a quadratic subunit of a TEM grid showing nearly cubic superlattice built up of cubic wuestite nanocrystals. b) SAED of a selected superlattice with uneven but symmetric intensity distribution caused by preferred alignment of the particles (orientational ordering). c) TEM image of aligned superlattices arising during deposition of cubic FeO nanocrystals in a magnetic field parallel to the substrate. d) TEM image of aggregated superlattices deposited without external magnetic field. Figure 6: a) TEM image of wuestite nanocrystals with seeds of magnetite inside. b) SAED of the material showing a speckled pattern for FeO reflections and diffuse rings for magnetite reflctions. c) Dark-field image of the region in Figure 5a (shown as negative); a part of the magnetite reflections were selected with the objective aperture. d) Dark-field image of the region in Figure 5a (shown as negative); a part of the wuestite reflections were selected with the objective aperture. Fe3O4 nanoparticles Sun et al, J. Am. Chem. Soc. 2004, 126, 273. Shape induce crystal alignment (14 nm MnFe2O4 nanoparticles) (100) texture (400) 16000 14000 Y Axis Title 12000 10000 8000 6000 4000 2000 (220) (311) 20 30 40 (511) (440) 50 60 70 80 2θ (100) texture H. Zeng, et al Dark Field Imaging of the Fe3O4 and FeO in TEM. Figure 6: a) TEM image of wuestite nanocrystals with seeds of magnetite inside. b) SAED of the material showing a speckled pattern for FeO reflections and diffuse rings for magnetite reflctions. c) Dark-field image of the region in Figure 5a (shown as negative); a part of the magnetite reflections were selected with the objective aperture. d) Dark-field image of the region in Figure 5a (shown as negative); a part of the wuestite reflections were selected with the objective aperture. Bimagnetic Core/Shell Nanoparticles Zeng et al, Nano Lett. 2004, 4, 187. Spin-dependent tunneling in Nanocrystal arrays Chuck Black, Bob Sandstrom, Chris Murray, Shouheng Sun I (pA) 400 T = 70 K T=2K 200 0 -200 -400 -0.4 shortest current path ~ 8 nanocrystals -0.2 0.0 V (V) 0.2 0.4 10 2 10 1 10 0 10 -1 10 -2 10 -3 1.00 20 40 60 80x10 -3 -1 1/T (K ) data fit by: ln(GV=0) = const. - Ec/kBT from fit to data, measure EC~ 10 meV for all devices measured, 10 meV < EC < 14 meV R/RH=0 GV=0 (1/GΩ) GV=0 follows simple thermal-activation H H 0.98 0.96 0.94 0.92 -0.4 -0.2 0.0 0.2 applied field (T) 0.4 Fe3O4 Nanocrystals (Sun and Zeng) 20 70 K 15 80 K H =0 H = 3.5 T 10 I (nA) 90 K 5 0 -5 -10 -4 -3 -2 -1 0 1 2 3 140 K -15 110 K 100 -20 -0.4 4 -0.2 0.0 0.2 0.4 VB (V) H (T) -0.26 -0.25 -0.28 -0.26 -0.27 -0.30 -0.28 MR MR (R(H)-R(0))/R(0) (%) 2 0 -2 -4 -6 -8 -10 -12 -14 -16 -18 -20 -0.32 -0.29 60 K -0.34 -0.6 -0.4 -0.2 0.0 0.2 0.4 0.6 Vb -0.30 100 K -0.31 -0.4 -0.3 -0.2 -0.1 0.0 0.1 0.2 0.3 0.4 Vb Potential for spintronic device applications Nanoparticle synthesis from self-assembled polymer templates • Diblock copolymer system PS/PMMA • Self-assembly promoted by heating • Removal of PMMA 100 nm metallization remove polymer C. Black, K. W. Guarini, R. L. Sandstrom, IBM Yorktown • T.Metal deposition