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  • 1
    Book
    Book
    Madrid : Instituto Español de Oceanografía
    Type of Medium: Book
    Pages: 71 S
    Series Statement: Informes técnicos / Instituto Español de Oceanografía 127
    Language: Spanish
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  • 2
    Type of Medium: Book
    Series Statement: Informes tecnicos / Instituto Espanol de Oceanografia 72
    Language: Undetermined
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  • 3
    Online Resource
    Online Resource
    Cambridge :Cambridge University Press,
    Keywords: Cosmochemistry--Congresses. ; Electronic books.
    Description / Table of Contents: This timely 2004 review of developments in cosmochemistry over the last decade is written by seven prestigious astrophysics researchers. It covers cosmological and stellar nucleosynthesis, abundance determinations in stars and ionised nebulae, chemical composition of nearby and distant galaxies, and models of chemical evolution of galaxies and intracluster medium.
    Type of Medium: Online Resource
    Pages: 1 online resource (314 pages)
    Edition: 1st ed.
    ISBN: 9780511187469
    Series Statement: Cambridge Contemporary Astrophysics Series
    DDC: 523.02
    Language: English
    Note: Cover -- Half-title -- Title -- Copyright -- Contents -- Participants -- Preface -- Acknowledgements -- Primordial Alchemy: From The Big Bang To The Present Universe -- 1. Introduction -- 2. The Early Evolution of the Universe -- 2.1. Redshift -- 2.2. Dynamics -- 2.2.1. Counting Relativistic Degrees of Freedom -- 2.2.2. "Extra" Relativistic Energy -- 3. Big Bang Nucleosynthesis and the Primordial Abundances -- 3.1. An Early Universe Chronology -- 3.1.1. Neutron - Proton Interconversion -- 3.1.2. Building The Elements -- 3.2. The SBBN-Predicted Abundances -- 3.3. Variations On A Theme: Non-Standard BBN -- 4. Observational Status of the Relic Abundances -- 4.1. Deuterium -- 4.2. Helium-3 -- 4.3. Helium-4 -- 4.4. Lithium-7 -- 5. Confrontation Of Theoretical Predictions With Observational Data -- 5.1. Deuterium - The Baryometer Of Choice -- 5.2. SBBN Baryon Density - The Baryon Density At 20 Minutes -- 5.3. CMB Baryon Density The Baryon Density At A Few Hundred Thousand Years -- 5.4. The Baryon Density At 10 Gyr -- 5.5. Baryon Density Concordance -- 5.6. Testing The Consistency Of SBBN -- 6. BBN In Non-Standard Models -- 6.1. Degenerate BBN -- 7. Summary -- REFERENCES -- Stellar Nucleosynthesis -- 1. Introduction -- 1.1. Nuclear Reactions -- 1.2. Stellar Evolution -- 2. Nucleosynthesis in Massive Stars -- 2.1. Yields from massive star models -- 2.2. Oxygen isotopes from massive stars -- 2.2.1. The O yields in massive star models -- 2.2.2. The O yield and stellar wind mass loss -- 2.2.3. The production of O as function of metallicity -- 2.2.4. How to produce O ? -- 2.2.5. Clues from oxygen -- 2.3. Pre-supernova surface abundances -- 2.4. Effects of Rotation -- 3. The s-Process -- 3.1. Low mass stars -- 3.2. Massive stars -- 4. Nucleosynthesis in Binary Systems -- 4.1. Aluminium in Massive Binaries -- 4.2. Progenitors of Type Ia Supernovae. , 4.2.1. Supersoft X-ray Sources -- 4.2.2. Helium shell flashes -- 4.2.3. White dwarf spin-up -- 4.2.4. Outlook -- 5. The Most Massive Stars -- 5.1. The Eddington limit -- 5.1.1. Does the Eddington limit apply in the stellar interior? -- 5.1.2. The Omega-limit -- 5.1.3. Rotating very massive stars -- 5.2. Evolution of very massive stars -- 5.3. Supermassive stars -- REFERENCES -- Observational Aspects Of Stellar Nucleosynthesis -- 1. Introduction -- 2. Stellar nucleosynthesis - A site survey -- 2.1. Sites -- 2.2. Surveying tools -- 3. Numbers and Notation -- 4. Pioneering Tales -- 4.1. Technetium in S Stars -- 4.2. The Spite Plateau -- 5. An Assumption and a Warning -- 6. Black Boxes and Black Magic -- 6.1. Why are abundance analyses incomplete? -- 6.2. Why does a line of E yield A(E) = n(E)/n(H)? -- 6.3. The Curve of Growth -- 7. Lithium, Beryllium, and Boron -- 7.1. Observational Constraints -- 7.2. Theoretical Proposals -- 7.3. Observed Abundances -- 7.3.1. Li-rich red giants -- 7.3.2. Lithium from Novae? -- 7.3.3. Galactic Evolution of Lithium -- 7.3.4. Galactic Evolution of Beryllium -- 7.3.5. Galactic Evolution of Boron -- 8. Stellar spectroscopy and the s-process -- 8.1. Introduction -- 8.2. Nuclear physics of the s-process -- 8.3. Operation of the s-process -- 8.4. AGB stars and the s-process -- 8.5. Weak s-process at low metallicities? -- 9. Concluding Remarks -- REFERENCES -- Abundance Determinations In H ii Regions And Planetary Nebulae -- 1. Introduction -- 2. Basic physics of photoionized nebulae -- 2.1. Ionization and recombination -- 2.1.1. Global ionization budget -- 2.1.2. The ionization structure -- 2.2. Heating and cooling -- 2.3. Line intensities -- 3. Basics of abundance determinations in ionized nebulae -- 3.1. Empirical methods -- 3.1.1. Direct methods -- 3.1.2. Strong line or statistical methods -- 3.2. Model fitting. , 3.2.1. Philosophy of model fitting -- 3.2.2. Photoionization codes -- 4. Main problems and uncertainties in abundance determinations -- 4.1. Atomic data -- 4.1.1. Ionization, recombination and charge exchange -- 4.1.2. Transition probabilities, collision strengths and effective recombination coeffcients -- 4.2. Stellar atmospheres -- 4.3. Reddening correction -- 4.4. Aperture correction, nebular geometry and density inhomogeneities -- 4.5. Spatial temperature variations -- 4.5.1. Temperature gradients -- 4.5.2. Small scale temperature variations -- 4.6. The optical recombination lines mystery -- 4.7. The role of internal dust -- 4.7.1. Evidence for the presence of dust in the ionized regions -- 4.7.2. Heavy element depletion -- 4.7.3. The effect of dust on the ionization structure -- 4.7.4. The effect of dust obscuration on the emission line spectrum -- 4.7.5. The effects of grains on heating and cooling of the gas -- 4.8. The specific case of the helium abundance determination -- 5. Observational results on abundances in H ii regions of the Milky Way -- 5.1. The Orion nebula: a benchmark -- 5.2. Abundance patterns in the solar vicinity and the solar abundance discrepancy -- 5.3. Abundance gradients in the Galaxy from H ii regions -- 5.4. The Galactic center -- 5.5. Nebulae around evolved massive stars -- 6. Observational results on abundances in planetary nebulae -- 6.1. NGC 7027 and IC 418: two test cases -- 6.2. What do PN abundances tell us? -- 6.3. PNe as probes of the chemical evolution of galaxies -- 6.3.1. The universal Ne/H versus O/H relation -- 6.3.2. Abundance gradients from PNe in the Milky Way -- 6.3.3. PNe in the Galactic bulge -- 6.3.4. PNe in the Galactic halo -- 6.3.5. PNe probe the histories of nearby galaxies -- 6.4. PNe probe the nucleosynthesis in their progenitor stars -- 6.4.1. Global abundance ratios. , 6.4.2. Abundance inhomogeneities -- REFERENCES -- Element Abundances In Nearby Galaxies -- 1. Introduction -- 2. Observational Methods for Measuring Abundances -- 2.1. Spectroscopy of H II Regions and Planetary Nebulae -- 2.1.1. Observational Considerations -- 2.1.2. The Direct Method -- 2.1.3. "Empirical" (Strong-Line) Calibrations -- 2.1.4. Photoionization Models -- 2.2. Spectroscopy of Individual Stars -- 2.3. Stellar Photometry and Color-Magnitude Diagrams -- 2.4. Spectrum Synthesis of Stellar Populations -- 2.5. Surface Photometry and Galaxy Colors -- 3. Abundances in Local Group Dwarf Elliptical Galaxies -- 3.1. Metallicities -- 3.2. Element Ratios -- 4. Abundance Profiles in Spirals and Irregulars -- 4.1. Gas and Stellar Masses -- 4.1.1. Neutral and Molecular Gas -- 4.1.2. Stellar Mass Densities -- 4.2. Spatial Abundance Profiles -- 4.3. Metallicity versus Galaxy Luminosity/Mass -- 4.4. Abundance Gradient Variations -- 4.5. Metallicity vs. Surface Brightness -- 4.6. Barred Spirals -- 4.7. Spiral Bulges -- 4.8. Cluster Spirals and Environment -- 5. Element Abundance Ratios in Spiral and Irregular Galaxies -- 5.1. Helium -- 5.2. Carbon -- 5.3. Nitrogen -- 5.4. Neon, Sulfur and Argon -- 5.5. Other Elements -- 6. Open Questions and Concluding Remarks -- REFERENCES -- Chemical Evolution Of Galaxies And Intracluster Medium -- 1. Basic parameters of chemical evolution -- 2. The stellar birthrate -- 2.1. Theoretical recipes for the SFR -- 2.2. The tracers of star formation -- 2.3. The IMF: Various Parametrizations -- 2.4. Derivation of the IMF -- 2.5. The Infall Rate: Various Parametrizations -- 3. Nucleosynthesis -- 3.1. Nucleosynthesis in the Big Bang -- 3.2. Stellar Nucleosynthesis -- 3.3. Supernova Progenitors -- 3.4. Element production -- 3.5. Stellar yields -- 4. Modelling chemical evolution -- 4.1. Analytical models. , 4.2. Failure of the Simple Model -- 4.3. Analytical models with gas flows -- 5. Equations with Type Ia and II SNe -- 5.1. Type Ia SN rates -- 6. The formation and evolution of the Milky Way -- 6.1. Models for the Milky Way -- 6.2. The two-infall model -- 6.3. Applications to the Local Disk -- 6.4. Applications to the whole disk -- 6.5. The Role of Radial Flows in the evolution of the Galactic Disk -- 6.6. The Role of the IMF in the evolution of the Galactic Disk -- 6.7. Scenarios for Bulge Formation -- 7. Disks of Other Spirals -- 8. Conclusions on the Milky Way and other spirals -- 9. Elliptical Galaxies -- 9.1. Observational properties -- 9.2. Formation of Ellipticals -- 9.3. Formation of Ellipticals at low z -- 9.4. Formation of Ellipticals at high z -- 9.5. Models for ellipticals based on galactic winds -- 9.6. Failure of Larson's Model -- 9.7. Averaged Stellar Metallicities -- 9.8. Multi-Zone Models -- 10. Conclusions on Ellipticals -- 11. Evolution of Dwarf Galaxies -- 11.1. Evidences for Galactic Winds -- 11.2. Results for BCG from chemical models -- 11.3. Results from chemo-dynamical models -- 11.4. Dwarf galaxies and DLA Systems -- 12. Chemical Enrichment of the ICM -- 12.1. Models for the ICM -- 12.2. MV88 Results -- 12.3. [α/Fe] Ratios in the ICM -- 12.4. [α/Fe] ratios and IMLR -- 13. Conclusions on the ICM -- REFERENCES -- Element Abundances Through The Cosmic Ages -- 1. Introduction -- 1.1. Some Basic Concepts -- 2. Damped Lyα Systems -- 2.1. What Are They? -- 2.2. Why Do We Care? -- 2.3. The Metallicity of DLAs -- 2.4. Element Ratios -- 2.4.1. Dust in DLAs -- 2.4.2. Alpha-capture elements -- 2.4.3. The Nucleosynthesis of Nitrogen -- 3. The Lyman Alpha Forest -- 3.1. Metals in the Lyα Forest -- 3.2. C IV at the Highest Redshifts -- 4. Lyman Break Galaxies -- 4.1. Stellar Populations and the Initial Mass Function. , 4.2. Element Abundances in the Interstellar Gas.
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  • 4
    ISSN: 1089-7550
    Source: AIP Digital Archive
    Topics: Physics
    Notes: We communicate a detailed study of the epitaxial growth of CeO2 on MgO. The key feature of the growth is the dependence of the in-plane orientation of the CeO2 epitaxial layer on the MgO surface morphology. Atomic force microscopic (AFM) measurements, x-ray analyses, as well as high-resolution transmission electron microscopy (HRTEM) investigations reveal that on rough substrates a cube-on-cube growth of CeO2 on MgO occurs while on smooth substrates the CeO2 unit cell is rotated around the surface normal by 45° with respect to the MgO unit cell when the deposition rate is low (∼0.3 A(ring)/s) during the first stages of growth. This growth mechanism can be used for a defined fabrication of 45° grain boundaries in the CeO2 layer by controlling the surface roughness of the MgO substrate. This report demonstrates that these 45° grain boundaries may be used to fabricate YBa2Cu3O7−x Josephson junctions. © 1995 American Institute of Physics.
    Type of Medium: Electronic Resource
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  • 5
    Electronic Resource
    Electronic Resource
    [S.l.] : American Institute of Physics (AIP)
    Journal of Applied Physics 79 (1996), S. 3337-3339 
    ISSN: 1089-7550
    Source: AIP Digital Archive
    Topics: Physics
    Notes: Epitaxial thin films of Y-doped SrZrO3 have been grown on MgO(001) by pulsed laser deposition. The deposition process has been performed at temperatures of 1000–1200 °C and at an oxygen pressure of 1.5×10−1 mbar. The samples are characterized by Rutherford backscattering spectrometry/channeling (RBS/C) and x-ray diffraction (XRD). We found an epitaxial relationship of SrZrO3 (0k0) [101](parallel)MgO (001) [100]. Good crystalline quality is confirmed by RBS/C minimum yield values of 9% and a FWHM of 0.35° of the XRD rocking curve. © 1996 American Institute of Physics.
    Type of Medium: Electronic Resource
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  • 6
    Electronic Resource
    Electronic Resource
    [S.l.] : American Institute of Physics (AIP)
    Journal of Applied Physics 61 (1987), S. 4358-4360 
    ISSN: 1089-7550
    Source: AIP Digital Archive
    Topics: Physics
    Notes: In order to study the local atomic environments of both B and Fe in Fe3B1−xCx (0.1≤x≤0.4), NMR measurements of the hyperfine field distributions for 10B, 11B, and 57Fe have been performed at 4.2 K and from 10 to 60 MHz. It was found that the 11B and 57Fe NMR frequencies do not change with C concentration. From these results, the 11B NMR frequency characteristic of orthorhombic Fe3B was unambiguously determined to be 36.3 MHz, which is in good agreement with the value obtained for the orthorhombic Fe3B phase prepared by annealing amorphous Fe80B20. Our results show that the substitution of C atoms for B atoms has a small effect on the hyperfine field at both the B and Fe nuclei as well as on the magnetic moment of the Fe atoms.
    Type of Medium: Electronic Resource
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  • 7
    Electronic Resource
    Electronic Resource
    [S.l.] : American Institute of Physics (AIP)
    Journal of Applied Physics 61 (1987), S. 4349-4351 
    ISSN: 1089-7550
    Source: AIP Digital Archive
    Topics: Physics
    Notes: The rapidly quenched, crystalline, Fe-rich Fe100−xMx system has been studied by 57Fe Mössbauer effect spectrometry. Boron and carbon alloys were found to have regions with cementite local structure. Small amounts of fcc γ-Fe were also observed in some of the cases. Furthermore, almost half of the carbon was concluded to be in interstitial solution. Upon annealing the carbon alloy, the fcc phase disappears to benefit formation of the cementite. In contrast, the alloys with aluminum, silicon, and phosphorous are substitutional solid solutions. After being annealed at 1073 K, they do not show changes in their hyperfine interactions nor in their crystalline structure. However, the lattice parameter of the alloy with phosphorous unexpectedly increased from a value below that corresponding to pure iron to another above it. These results are discussed on the basis of the metalloid solubilities in iron and their atomic sizes.
    Type of Medium: Electronic Resource
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  • 8
    Electronic Resource
    Electronic Resource
    [S.l.] : American Institute of Physics (AIP)
    Journal of Applied Physics 61 (1987), S. 3231-3233 
    ISSN: 1089-7550
    Source: AIP Digital Archive
    Topics: Physics
    Notes: Based on a knowledge of the NMR spectra for FeB, Fe2B, orthorhombic Fe3B (o-Fe3B), and body-centered-tetragonal Fe3B (bct-Fe3B), the phases produced during the annealing of Fe-B amorphous alloys can be identified with greater sensitivity by NMR techniques than by x-ray diffraction. In the present work, a combination of x-ray diffraction experiments and spin-echo NMR measurements of the hyperfine field distributions for the 10B, 11B, and 57 Fe nuclei has been performed on both as-quenched and annealed Fe100−xBx (14≤x≤25) amorphous alloys. In general terms, it was found that annealing at temperatures near 400 °C resulted in crystallization products which included bct-Fe3B, while annealing at approximately 800 °C leads to the formation of o-Fe3B. The behavior of the B hyperfine field indicates that, for the Fe100−xBx amorphous alloys, an o-Fe3B-like local order is favored in the low B concentration regime, and a bct-Fe3B-like local order is favored in the high B concentration regime.
    Type of Medium: Electronic Resource
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  • 9
    Electronic Resource
    Electronic Resource
    [S.l.] : American Institute of Physics (AIP)
    Journal of Applied Physics 66 (1989), S. 1671-1675 
    ISSN: 1089-7550
    Source: AIP Digital Archive
    Topics: Physics
    Notes: The crystallization of Fe100−xBx amorphous alloys (x=14, 20, and 25), prepared by rapid quenching from the melt, was studied by Mössbauer effect spectroscopy. In general, the present results support recent nuclear magnetic resonance studies (performed on the same samples used in this work), which indicated that the amorphous material had a body-centered-tetragonal Fe3B-like short-range order for x=25 but an orthorhombic Fe3B-like one for x=14. For x=25, annealing at about 400 °C led to the formation of almost pure body-centered-tetragonal Fe3B. On the other hand, thermal treatments at about 800 °C produced a mixture of phases for all the compositions. For x=14, formation of body-centered-tetragonal Fe3B was not observed in any case. In addition, the present Mössbauer results, combined with the previous nuclear magnetic resonance ones, show that boron and iron atomic surroundings evolve differently when alloys with x=14 are annealed at 390–420 °C. In the boride phase, the 57Fe Mössbauer signal remained "amorphouslike'' in contrast with the 11B nuclear magnetic resonance signals which became sharp and corresponded to those in tetragonal and orthorhombic Fe3B and in Fe2B. These results would indicate that under these experimental conditions the surroundings of the boron atoms become ordered before the surroundings of the iron atoms.
    Type of Medium: Electronic Resource
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  • 10
    Electronic Resource
    Electronic Resource
    [S.l.] : American Institute of Physics (AIP)
    Journal of Applied Physics 66 (1989), S. 875-880 
    ISSN: 1089-7550
    Source: AIP Digital Archive
    Topics: Physics
    Notes: The transformation of the Fe0.91B0.09 rapidly quenched crystalline alloy from its original metastable state to its equilibrium state has been studied by Mössbauer effect spectroscopy. It was found that the alloy transforms in a single step from a fine dispersion of orthorhombic-Fe3B-like complexes embedded in metallic bcc iron to a system consisting of Fe2B precipitates in the α-Fe matrix. The kinetics and temperature dependence of the process have been measured. It was determined that the relative fraction of Fe2B increases as Ω=1−exp(−kt3/2) with k=k0 exp(−Ea/kBT), indicating a diffusion-controlled, Arrhenius-type transformation, where k0=(1.92±0.26)×1014 s3/2 and Ea=(3.56±0.07) eV/atoms. Magnetization versus temperature scans have been simulated and compared to previously measured scans. A simple picture of the transformation process is given.
    Type of Medium: Electronic Resource
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