The “Flying Man,” Otto Lilienthal, demonstrated in the early 1890s that man can fly with artificial wings, but his success with monoplanes depended on constant body movement, requiring strength, flexibility, agility, coordination and endurance. After studying Lilienthal’s effort, Chanute wanted his flying machine to be perfectly manageable, automatically stable and strong enough in every part to make it safe and easy to fly. His biplane glider, developed and flown in the Indiana Dunes in the summer of 1896, proved to be a key step in the evolution of the flying machine. Believing that it could be the prototype for other enthusiasts, Chanute became the conduit of encouragement. In the decade to follow, almost every famous, and not so famous, aeronautical enthusiast obtained and used the readily available drawings of the biplane glider to first build one and then experience flying and gravity, before introducing their skills and imagination to improve the design.

This chapter details Octave Chanute's contributions to the effort to develop flying machines. By the early days of the twentieth century, the ancient taboo of flight slowly emerged as a thoroughly modern inquiry of science. To realize his personal goal of witnessing sustained mechanical flight, Chanute freely shared what he had learned; for him, technical information was a public commodity and he impressed on his correspondents the need to share what they had discovered so that future investigators could avail themselves of the known and take problems to the next level. By linking his many correspondents into an informal network, Chanute provided motivation and became the focal point of a far-reaching international community of flying machine experimenters.

This chapter details the early years of Octave Chanute. In 1838, six-year-old Octave arrived in America with his father Joseph Chanut, who had accepted an offer to teach in one of the three major colleges in antebellum Louisiana. The eldest of three, Octave left the security of his life in Paris, where he lived with his mother, grandmother, and two younger brothers, to move to America with a father he barely knew. A new life, so different and not Parisian at all, began for Joseph and Octave. Joseph home-schooled his son, and his French-speaking colleagues supplied a teaching curriculum according to their expertise, usually communicating in their mother tongue. They not only taught the youngster to read and write, but also to tell the truth and observe the general rules of etiquette. In September 1846, Octave entered the Coudert Lyceum in New York for an education different than what he had received from his father and other professors in Louisiana. After graduating in August 1848 with a degree similar to a high school diploma, Octave selected the Hudson River Railroad as his path into the future.

The English engineer Sir George Cayley worked out the basic principles of the aircraft at the turn of the 19th century. The German mechanical engineer Otto Lilienthal realized that building a successful aircraft required learning how to fly first. The American civil engineer Octave Chanute learned from his many predecessors that mechanical flight was certainly within the range of possibilities. As a careful designer and critical analyst, he progressed systematically by observing and interpreting the behavior of his various glider designs in flight, an essential step in the initial development of the aeroplane. Following in the footsteps of his predecessors, Chanute began an ambitious aerodynamic research program in the summer of 1896. It is a unique opportunity to reflect on the happenings of more than a century ago when few believed that flight is probable.

The crystal structure of PrCoO3 has been studied with high-resolution neutron powder diffraction and pair-distribution-function analysis in the temperature range from 12-600 K. The compound has the orthorhombic (Pbnm) perovskite structure over the entire temperature range. The temperature dependence of the average Co-O bond length shows clear anomalies near 60 K and 200 K where anomalous temperature dependencies of thermal conductivity and magnetic susceptibility have been reported. The data show a constant intermediate-spin-state fraction within 60 < T < 200 K and excitation of high-spin-state Co(III) above 200 K.

French-born and self-trained civil engineer Octave Chanute designed America's two largest stockyards, created innovative and influential structures such as the Kansas City Bridge over the previously “unbridgeable” Missouri River, and was a passionate aviation pioneer whose collaborative approach to aeronautical engineering problems helped the Wright brothers take flight. Drawing on a trove of archival material and exclusive family sources, this book is the first detailed examination of Chanute's life and his immeasurable contributions to the fields of engineering and transportation, from the ground transportation revolution of the mid-nineteenth century to the early days of aviation. This book brings to light many previously overlooked facets of Chanute's life, in both his professional accomplishments and his personal relationships. Through the reflections of other engineers, scientists and pioneers in various fields who knew him, the book characterizes Chanute as a man who believed in fostering and supporting people who were willing to learn. This biography cements Chanute's place as a preeminent engineer, pioneer, and mentor in the history of transportation in the United States and the development of the airplane.

We report the synthesis of Sr1-xCaxMnO3 and La0.5Ba0.5MnO3 perovskites over extended cation and oxygen composition ranges and describe the dependence of their phase stability on the tolerance factor t = t(x,T,δ) that is a function of composition, temperature, and oxygen content. We show that magnetic transition temperatures depend strongly on the tolerance factor and charge disorder while dependence on the structural disorder is less important. By reducing charge and structural disorder we have significantly increased the Curie and Neel temperatures for perovskite manganites.

Introduction by Tom D. Crouch: Octave Chanute and Course of Human Prologue Book 1 The Formative Years Book 2 The University of Experience, Starting an Engineering Career Book 3 Opening The West Book 4 At the Top Book 5 Self Realization Book 6 Preserving Timber, Business Owner and Consulting Engineer Book 7 From the Locomotive to the Aeromotive Book 8 Encouraging Progress in Flying Machines Acknowledgments Endnotes and References Index

The structure, magnetism, transport and thermal expansion of the perovskite oxide LaNi0.5Fe0.5O3 were studied over a wide range of temperatures. Neutron time-of-flight data have shown that this compound undergoes a first-order phase transition between ∼275 and ∼310K. The structure transforms from orthorhombic (Pbnm) at low temperatures to rhombohedral (R3¯c) above room temperature. This phase transition is the cause for the previously observed co-existence of phases at room temperature. The main structural modification associated with the phase transition is the change of tilting pattern of the octahedra from a+b−b− at low temperatures to a−a−a− at higher. Magnetic data strongly suggests that a spin-glass magnetic state exists in the sample below 83K consistent with the absence of magnetic ordering peaks in the neutron data collected at 30K. At high temperatures the sample behaves as a small polaron electronic conductor with two regions of slightly different activation energies of 0.07 and 0.05eV above and below 553K, respectively. The dilatometric data show an average thermal expansion coefficient of 14.7×10−6K−1 which makes this material compatible with frequently used electrolytes in solid oxide fuel cells.

R2-xNdxMo4O15 solid solutions (R=Ho, Dy, 0 <= x <= 0.6) were successfully prepared and their structures investigated by X-ray powder diffraction, in comparison with those of solid solutions with R=Er and Y. All these molybdates crystallise in the monoclinic space group P2(1)/c. The maximum values of x for R=Er, Y, Ho and Dy were found to be 0.6, 0.4, 0.4 and 0.0 respectively. The thermal expansion properties of R2Mo4O15 and R1.8Nd0.2Mo4O15 (R=Er, Y, Ho, Dy) were studied using high temperature X-ray diffraction in the range 25-500 degrees C. Nd substitution increased the thermal expansion coefficient (TEC); for x=0.2, the TEC for R1.8Nd0.2Mo4O15 increases by 27.9, 6.0 and 3.2% for R=Er, Y and Ho respectively. Bond length analysis shows that the weak Mo2 center dot center dot center dot O14 bond is likely to control the thermal expansion behaviour of these molybdates.

Time-of-flight neutron powder diffraction data for NIST Standard Reference Materials have been used to study the adequacy of the peak profile model obtained from a convolution of back-to-back exponentials with a pseudo-Voigt function that is widely used in Rietveld refinement. It is shown that, while the empirical models ford-spacing (wavelength) dependence of Gaussian and Lorentzian components of the pseudo-Voigt function and rise exponent are satisfactory, the behavior of the decay exponent and peak positions demonstrate significant deviations, which can be corrected by numerical methods. The practical side of this process as implemented inGSASandFULLPROFand the effect of the corrections on the Rietveld analysis results are discussed.

Structures, thermal expansion properties and phase transitions of ErxFe2−x(MoO4)3 (0.0≤x≤2.0) have been investigated by X-ray diffraction and differential thermal analysis. The partial substitution of Er3+ for Fe3+ induces pronounced decreases in the phase transition temperature from monoclinic to orthorhombic structure. Rietveld analysis of the XRD data shows that both the monoclinic and orthorhombic Fe2(MoO4)3, as well as the orthorhombic ErxFe2−x(MoO4)3 (x≤0.8) have positive thermal expansion coefficients. However, the linear thermal expansion coefficients of ErxFe2−x(MoO4)3 (x=0.6–2.0) decrease with increasing content of Er3+ and for x≥1.0, compounds ErxFe2−x(MoO4)3 show negative thermal expansion properties. Attempts for making zero thermal expansion coefficient materials result in that very low negative thermal expansion coefficient of −0.60×10−6/°C in Er1.0Fe1.0(MoO4)3 is observed in the temperature range of 180–400°C, and zero thermal expansion is observed in Er0.8Fe1.2(MoO4)3 in the temperature range of 350–450°C. In addition, anisotropic thermal expansions are found for all the orthorhombic ErxFe2−x(MoO4)3 compounds, with negative thermal expansion coefficients along the a axes.

The syntheses and structures of Er2−xCexW3O12 were studied. It was found that pure phases could form only for 0.0≦x≦0.4 and 1.5≦x≦2.0. Compounds with 0≦x≦0.4 have the hydrated orthorhombic structure at room temperature and transform to unhydrated orthorhombic one above 135°C whereas samples with 1.5≦x≦2.0 crystallize in monoclinic structure. Thermal expansion properties of Er2−xCexW3O12 were studied with high temperature X-ray powder diffraction. Samples with 0≦x≦0.4 exhibit negative thermal expansion in temperature range of 200–800°C and higher cerium content leads to more negative thermal expansion coefficient. However, compounds with 1.5≦x≦2.0 show positive thermal expansion owing to the edge-sharing polyhedra.

Zr-rich, Nb-doped lead zirconate titanate ceramic and powder samples with composition near Pb-0.99(Zr0.95Ti0.05)(0.98)Nb0.02O3 [PZT95/5(2Nb)] have been studied in the range of hydrostatic pressure 0-6.2 kbar and temperature 12-295 K by time-of-flight neutron powder diffraction and dielectric measurements. The combination of the two techniques has led to further insights into the properties and pressure-induced ferroelectric rhombohedral R3c (F-R(LT)) to antiferroelectric orthorhombic Pbam (A(O)) phase transition in this material, and the diffraction results have provided a detailed view of the ionic displacements induced by changes in pressure and temperature as well as the displacements accompanying the transition. At 295 K the diffraction results revealed a sharp transition at 2.1 kbar; at 200 K this transition occurs at 1.1 kbar. The transformation is incomplete: after the initial sharp drop in the F-R(LT) content at the transition, 20 wt % of the sample remains in the low-pressure F-R(LT) phase. Above the transition, the fraction of F-R(LT), which exists as a minority phase in the high-pressure A(O) phase, continues to decrease, but even at our highest pressure of 6.2 kbar, similar to 8 wt % of the sample remains in the F-R(LT) phase. The volume contraction at the F-R(LT)-to-A(O) transition unexpectedly results in the retained minority F-R(LT) being anisotropically "clamped," with its a axis slightly expanded and c axis contracted at the transition. On pressure release to 1 bar at 295 K, only 26% of the F-R(LT) phase is recovered, and this remains in the clamped state because of the surrounding majority A(O) phase. Heating the sample above 350 K at 1 bar followed by cooling to room temperature results in full recovery of the F-R(LT) phase. The spontaneous polarization (P-S) of the F-R(LT) phase and its pressure and temperature dependences were determined from the ionic displacements. At 295 K, P-S=38 mu C/cm(2)-a value greater than the 31-32 mu C/cm(2) commonly observed on ceramic PZT95/5(2Nb) samples. The difference is undoubtedly related to residual porosity in ceramic samples as well as the inability of the poling electric field to align all the polar domains. P-S increases monotonically with decreasing temperature, reaching a value of similar to 44 mu C/cm(2) at 12 K.

We have investigated the crystal and magnetic structure of the RPd2Al2 compounds (R=La, Ce) by neutron powder diffraction (ND) and inelastic neutron scattering (INS). The ND study shows that both compounds undergo a structural phase transition from tetragonal to orthorhombic symmetry at 91.5 K (La) and 13.5 K (Ce). In the case of CePd2Al2 the crystal field excitation spectrum, which has an extra peak that cannot be explained by a standard crystal field model, indicates the presence of strong magneto-elastic coupling.

Effects of the substitution of nontransition metal Al on phase transition, crystal structures, and magnetic properties of Nd3(Fe,Ti)29-type intermetallics have been systematically investigated by means of x-ray diffractions, time-of-flight powder neutron diffraction, and magnetic measurements. Rietveld analyses of x-ray diffraction patterns indicate that Nd3Fe27.5−xTi1.5Alx compounds mainly crystallize in Nd3(Fe,Ti)29-type structure (A2∕m space group) when x⩽1.5, but the main phase was replaced by Th2Zn17-type structure (R3¯m space group) when x>1.5. The lattice parameters a, b, c, and unit cell volume V of 3:29 phase in Nd3Fe27.5−xTi1.5Alx increase linearly with the substitution of Al. The site distributions of Ti and Al atoms were determined by refining the powder neutron diffraction data and it was found that Ti atoms prefer to occupy 4i1, 4i2, and 4g sites with the largest number of Fe neighbors while Al atoms prefer to take 4i4 and 8j4 sites with the largest number of rare earth neighbors. The Curie temperature of Nd3Fe27.5−xTi1.5Alx increases monotonously while the saturated magnetization decreases almost linearly with increasing Al content (x⩽1.5).

Time-of-flight powder neutron diffraction combined with Rietveld analysis was used to study Sc2W3O12 at pressures of up to 0.6 GPa in a large volume helium gas cell. Orthorhombic (Pnca) Sc2W3O12, bulk modulus 32(3) GPa, transforms to a softer monoclinic (P21/a) structure, 11.8(8) GPa, on compression at between 0.25 and 0.30 GPa. This transition shows significant hysteresis and involves a volume reduction of ∼1.5%. The volume reduction during compression of the orthorhombic phase is much less anisotropic than that induced by heating this negative thermal expansion phase at ambient pressure. While the volume reduction on heating orthorhombic Sc2W3O12 is associated with pronounced changes in Sc O W angles, there are no major changes in these angles on compression to similar densities. The structural changes seen at the pressure induced orthorhombic to monoclinic transition in Sc2W3O12 are similar, although not identical, to those seen for the equivalent thermally induced transition in Sc2Mo3O12.