Inventor(s): Abdelaziz Rahy (Waxahachie, TX), Raynard Rene Veldman (Mansfield, TX) Assignee(s): Magnablend, Inc. (Waxahachie, TX) Law Firm: Brinks Gilson Lione (7 non-local offices) Application No., Date, Speed: 15110545 on 01/07/2015 (1434 days app to issue)

The locations of ancestral Native Americans between ~20,000 and 15,000 years ago remain unknown, but two scenarios have been proposed (19). Scenario 1 posits that the split of Ancient Beringians and other Native Americans occurred in northeast Asia/Siberia, while scenario 2 posits that this split occurred in eastern Beringia (Alaska). Current archeological and paleoecological data support scenario 1. There is no secure evidence of ~20,000-year-old American sites, while there is abundant evidence of human occupation in northeast Asia (for example, southern Siberia, Amur basin, Primor’ye, and Japanese archipelago) (fig. S1) (23). The LGM is regionally characterized by very cold and arid conditions with evidence for depopulation of north Asia and no evidence throughout Eurasia for northward expansions of humans (24, 25). Previous genetic models of Native American demography indicate a bottleneck during this period, with expansion only after 16,000 to 13,000 years ago (13, 26). We observe a clear pattern of human expansion from Siberia to Beringia around 16,000 to 14,000 years (12) and the first unequivocal and widespread occupations south of glacial ice in the Americas after 13,500 years ago, associated with Clovis and Fishtail complex technologies (27–29). We note that both point types are continent-wide in North and South America, respectively. They are the only point types with such broad distributions and are consistent with colonizing processes (30–32), although they might also represent communication of ideas among low-density early populations.

Mr. Cochran was born Oct. 18, 1953 in Rome, son of Robert Lee Cochran Sr. and the late Ruth Wade Cochran.

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[F21V] FUNCTIONAL FEATURES OR DETAILS OF LIGHTING DEVICES OR SYSTEMS THEREOF; STRUCTURAL COMBINATIONS OF LIGHTING DEVICES WITH OTHER ARTICLES, NOT OTHERWISE PROVIDED FOR [7]

MGT nanocomposites were prepared through a layer-by-layer coating process (23). Magnetic Fe3O4 NPs were prepared through modified solvothermal reaction by reduction of FeCl3 (23). As shown in transmission electron microscopy (TEM) images (fig. S1A), the as-prepared Fe3O4 NPs were highly uniform with diameters of 120 ± 5 nm. We observed a well-resolved lattice fringe with an interplanar distance of 0.26 nm for Fe3O4, which corresponds to the (311) plane of magnetite (fig. S1B). In addition, hysteresis loops of Fe3O4 particles in fig. S1C indicate high-performance magnetic properties without remanence or coercivity at 300 K. We coated Fe3O4 NPs with GO through electrostatic adsorption with the linkage of polydimethyldiallylammonium chloride (PDDA) to produce magnetic Fe3O4@GO (MG). Scanning electron (SEM) micrographs (Fig. 2A) show that Fe3O4 NPs were effectively coated with GO. TEM images show that the irregular shapes of the nanocomposites were highly dispersed with diameters of 150 to 250 nm (Fig. 2B). Then, we prepared the uniform porous TiO2 shell via a versatile kinetics-controlled coating method to produce MGT nanocomposites. We observed the ternary heterostructure of MGT (size, 200 to 400 nm) coated by the aggregated TiO2 NPs (~8 nm) and with uniform pores (~5 nm; Fig. 2, C and D). N2 sorption isotherms (Fig. 2E) of the nanocomposites after calcination show typical type IV curves with distinct hysteresis loops close to the H1 type. The Brunauer-Emmett-Teller surface area and the pore volume of the as-prepared nanostructures were calculated to be as high as 105 m2 g−1 and 0.16 cm3 g−1, respectively. The corresponding pore size distribution curves (Fig. 2F) derived from the adsorption branches of the isotherms using the Barrett-Joyner-Halenda method show a sample pore size of ~4.3 nm, which was similar to that obtained from the SEM image. A high-resolution TEM (HR-TEM) image [Fig. 2G (III)] shows that the TiO2 NPs were crystallized with a well-resolved lattice fringe with an interplanar distance of 0.24 nm, which corresponds to the (103) plane of anatase (24). We carried out energy dispersive spectroscopy (EDS) to characterize the elemental composition and the structural relationship of the nanostructures from every step obtained (Fig. 2G). It was clear that Fe was located at the center of nanocomposites, while the shell contained C and Ti, which were well separated from each other. X-ray diffraction (XRD) fitted well to those of Fe3O4, GO, and TiO2 bulk phases (Fig. 2H). The diffraction peaks of Fe3O4 were ascribed to the (220), (311), and (440) planes. After Fe3O4 was coated with GO and TiO2, two additional diffraction peaks were observed at 21.2° and 43.3°, which should be ascribed to GO. Several new diffraction peaks appeared at 25.3°, 37.8°, 38.6°, 48.1°, 53.9°, and 55.1°, assigned to the (101), (004), (112), (200), (105), and (211) planes of anatase-phase TiO2, respectively (25, 26), confirming the successful preparation of MGT. We further used Raman and Fourier transform infrared (FTIR) spectroscopy to characterize the as-prepared MGT. As depicted in Fig. 2I, three distinct peaks at 397, 518, and 640 cm−1 in the Raman spectrum of MGT were observed, indicating the presence of anatase-phase TiO2 (26, 27). In the FTIR spectra of MGT (Fig. 2J), two additional infrared bands assigned to Ti–O–C at 1680 cm−1 and Ti–O–H stretching vibration at 3260 cm−1 were observed (28). Both Raman and FTIR results indicated that the MGT nanocomposites were successfully synthesized. The stepwise assembly of MGT was also monitored by microeletrophoresis measurements whose results were expressed as ζ-potentials (fig. S1D). Because of the superparamagnetic properties of the magnetic cores of MGT (Fig. 2K), the MGT nanocomposites were conveniently separated from the reaction solution after the photodegradation treatment upon application of an extended magnetic field. Moreover, it is known that TiO2 shows absorption ranging from 200 to 350 nm. On the other hand, absorbance of MGT nanocomposites extended to the visible region (400 to 600 nm) because of the conjugation of TiO2 with visible GO (fig. S1E) (26). Figure S2 shows the Raman spectra of copper phthalocyanine (CuPc) before and after illumination under visible light (460 nm < λ < 700 nm, 1000 W) on MGT nanocomposites. The intensity of the Raman spectra of CuPc sharply decreased after illumination by visible light for 90 min, revealing that CuPc was significantly photodegraded (26). In contrast, we obtained negligible changes for MT NPs (fig. S2, B and C). Accordingly, after five cycles of enrichment followed by illumination, the SERS activity of MGT remained more than 98% (fig. S2D), confirming the good recyclability of MGT. Considering the photocatalytic activity of MGT under the visible light region, we investigated the Raman signal reproducibility of MGT in fig. S3. After irradiating 15 times with an exposure time of 1 s, the Raman intensity of CuPc remained approximately 97%, indicating the high stability and reproducibility of MGT substrates. Besides, we measured the surface wettability of MGT through contact angle. As shown in fig. S1F, MGT showed hydrophilic properties with an MGT contact angle of 41° ± 2°, which is suitable for further bio-applications.

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First, because the surface of Fe3O4 NPs was rich in carboxyl, the surface charge of Fe3O4 NPs needed to be changed from negative to positive by PDDA. In a typical synthesis, about 5 mg of the prepared Fe3O4 NPs were dispersed in 15 ml of water and mixed with 5 ml of 1% PDDA solution. Then, the mixture was treated with ultrasonication for 30 min at room temperature. After that, 5 ml of the as-prepared GO was added to the mixture. With another 30 min of ultrasonic treatment, the MG nanocomposites were synthesized with a high yield. Last, the products were washed three times with DI water and ethanol with magnetic separation, respectively. The final precipitate was dispersed in 5 ml of ethanol for further use.

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