id stringlengths 7 10 | image imagewidth (px) 4 733 | query stringclasses 1
value | answers stringlengths 7 66.1k |
|---|---|---|---|
train_100 | What is described in this image? | 3.2. The behaviors of phase transition of silica in diatomite 3.2.1. XRD analysis of the sintered samples Powder X-ray diffraction (XRD) is one of the primary techniques used for tracking changes in the layer spacing and new phase formation of crystalline phase [15]. Fig. 5 shows the XRD patterns of diatomite calcined at different temperatures without or with flux. At low temperature below 1000 ℃ without flux (Fig. 5a), there was a broad diffraction peak existing between 15° and 30°, which meant the amorphous opal was still the same as the main phase composition of sintered sample, with a small quantity of quartz within. A new crystalline phase cristobalite began emerging at 1000 °C for the appearance of the '101', '200', Compared with non-flux calcination, the phase transition temperature from opal to cristobalite decreased by about 200 °C (Fig. 5b) under flux calcination, which meant the flux (Na>CO3) could facilitate the transformation of opal to cristobalite. Similarly, the diffracted intensity of the '101' plane of quartz also reduced continuously as the heating temperature exceeded 800 °C, especially when the temperature increased from 1100 °C to 1200 °C. Fig. 5. XRD patterns of diatomite calcined at different temperature; (a) without flux, (b) with flux. decreased continuously when the heating temperature exceeded 800 °C (Fig. 5b). There was about 64.02% content of quartz in raw diatomite turning to cristobalite by flux calcination from 1100 °C to 1200°C using Eq. (2), where cristobalite could only exist as a metastable phase out of its stable field. The most possible reason could be predicted the quartz in raw diatomite was inclined to transform into cristobalite rather than tridymite because of the existence of crystal nucleus of cristobalite formed from opal in calcined diatomite. | |
train_101 | What is described in this image? | which undoubtedly confirms that the material is X-ray amorphous (see Fig. 1a), similarly to a Cu44Zr47Al9 composition (d = 4 mm) [44]. The corresponding linear heating DSC curve exhibits typical features of a glass, including the glass transition (Tx = 671 K) followed by a two-stage crystallization sequence characterized by Tx1=759 K and Tx2=860 K transformation temperatures (see Fig. 1b), similar to the values obtained for other Cu-Zr-type BMGs. [39, 45, 46]. The width of supercooled liquid region ΔTx =80 K (ΔTx = Tx1, onset = Tg) of the glass Fig. 1 a X-ray diffraction patterns of as-cast Cu32Zf54Alg metallic glass and states achieved by continuous heating. b Continuous-heating DSC curve of the as-cast BMG obtained at 20 K min-1. The inset shows the melting and solidification of the alloy. e Continuous heating DSC curves obtained at different heating rates. d Kissinger plots obtained from the shift of the Tx1 and Tx2 transformation peak temperatures as a function of heating rate The obtained values corresponding to the exothermal heat release (△H1=67 Jg-1 and △H2=50 Jg-1) are practically independent of the heating rate. As obtained from the inset of Fig. 1b, the liquidus temperature (T) determined from the high temperature DTA curve is 1173 K. Since the Cu38ZI 4Als composition is off-eutectic, the melting endotherms and the freezing exotherms turns into a multi-step process. To further investigate the GFA of the Cu38ZI54Als composition, additional parameters have also been determined. The calculated reduced glass transition temperature I = T./T1 (0.57) also indicates that the Cu38Zr54Al8 system is an excellent glass former, similarly to other CuZr-based systems [46]. A much better interrelationship with the GFA incorporating both amorphization and devitrification processes has been introduced by Lu and Liu [48]. Evolution of the microstructure during the crystallization sequence can be inferred form the corresponding XRD patterns (Fig. 1a). As one can notice, linear heating above the first crystallization event (T iin1 = 810 K) results in a complete disappearance of the amorphous background, on the other hand the pattern is dominated by hexagonal CuZr (JCPDS 01-071-7931, a=0.5035 nm, c=0.3142 nm) Figure 1c focuses on the variation of the Tx1 and Tx2 peak temperatures with the applied heating rate. As being thermally activated processes, the individual crystallization events are expected to shift to higher temperatures with increasing heating rate, as confirmed by Fig. 1c. Among several models, the Kissinger analysis is extensively used to determine the activation energy (E2) of thermally activated processes [50]. As known, the dependence of the transformation peak temperatures (Ti) on the heating rate can be given by the β T Figure 1c focuses on the variation of the Tx1 and Tx2 peak temperatures with the applied heating rate. As being thermally activated processes, the individual crystallization events are expected to shift to higher temperatures with increasing heating rate, as confirmed by Fig. 1c. Among several models, the Kissinger analysis is extensively used to determine the activation energy (E2) of thermally activated processes [50]. As known, the dependence of the transformation peak temperatures (Ti) on the heating rate can be given by the β T Expression, where Z and R are the frequency factor and the gas constant, respectively [50]. Plotting In(B/T2) versus T =1 enables the determination of E i for each thermal event from the slope of the fitted straight line, see Fig. 1d. The obtained values (Ea,x1 =325 kJ mol-1, Ea,x2=210 kJ mol-1) Isothermal annealing treatments of the as-cast Cu38ZI54Al8 glass were carried out to understand better the nucleation mechanism in detail. The isothermal DSC curves obtained at different Tiso annealing temperatures in the range of 710-730 K are presented in Fig. 2a. As marked by arrows in Fig. 1b, these Tis temperatures are significantly lower than Tx1 and found within the ATx supercooled liquid range. As seen, each isotherm starts with an incubation period which is followed by a single exothermic peak. This shape of isotherms corresponds to a crystallization process that occurs through the formation of nuclei from the amorphous matrix followed by a growth mechanism [52]. This is in correlation with Fe-based BMGs [53], however, in contrast to Albased glasses, which exhibit a monotonically decreasing exothermic DSC signal with no clearly defined exothermic peaks [54]. The length of the incubation time (to) as well as the peak positions (tpeak) strongly varies with Tiso, i.e., the peak maximum occurs at shorter times at higher annealing temperature. The corresponding data are presented in Table 1. From the slope of the In(tpeak) versus Tiso-1 function The structure of the isothermally annealed states of the Cu38ZI54Al8 BMG was also examined by XRD. As confirmed by Fig. 2c, the patterns recorded after isothermal annealing exhibits the presence of the same crystalline phases, i.e., CuZI2 and CuZr as were obtained after a continuous heating above the first crystallization event (Tim=810 K), see also Fig. 1a. Similar results have been obtained recently for a Cu475Z45.1Al74 BMG [55]. The mean crystallite size of these two phases obtained after isothermal annealing shows some variation with Tjso, i.e., lower annealing temperature yields the formation of slightly larger nanocrystals, see Table 1. In spite of the similar devitrification products obtained after linear heating above the first crystallization peak (Thin1=810 K) and after isothermal annealings at Tiso =710-730 K, the different enthalpy release may correspond to the different average size of the crystallite products and to the different time scale of the two processes. | |
train_102 | What is described in this image? | Figure 7. Experimental plot of In Ti / B versus 1000/ Tp (for both two separated peaks (a) and (b)) straight regression lines of Ge10As20Te70, alloy (B in K s=1) | |
train_103 | What is described in this image? | Moreover, they are mechanically strong, solvent resistant, and environmentally stable. One major drawback of thermosetting polymers, including SMPs, lies in processing. By introducing catalyst to accelerate transesterification at high temperature, the resulted covalently cross-linked epoxy which was able to change its permanent shapes was invented.[27] This kind of covalent adaptive material is called vitrimer.[27-32] We here show that vitrimers can provide a flexible and effective strategy to achieve multishape memory effect. As illustrated in Figure 1a, premade MS, and BP), as shown in Figure 1b. They are all diglycidyl ether cured with diacids. The same amount of transesterification catalyst 1,5,7-triazabicylo[4.4.0]dec-5-ene (TBD) is used.  According to differential scanning calorimetry (DSC) measurement (Figure 1c), BA has a glass transition (To) around 30 ℃. (Figure 1d) with a shape recovery rate of =99%. Both MS and BP are smectic liquid crystalline networks (Please refer to Figure S4, Supporting Information, for the characterization of liquid crystalline phases). MS has a Tx at about 30 ℃ and a liquid crystalline isotropic transition (T) at about 65 ℃. BP (Tg ~ 50 ℃, and Ti ~ 100 ℃) has been used in our previous paper.[34] As we previously reported, BP demonstrates both triple-shape memory effect and two-way reversible shape memory effect under external load due to the presence of smectic-isotropic phase transition.[35-38] The shape memory behavior of MS is similar to BP, with lower response temperatures owing to lower Tg and T. Its triple-shape memory effect and two-way reversible shape memory effect of one cycle are shown in Figure 1e,f. The repeatability of these shape memory effects can be found in Figure S1-S3 (Supporting Information). | |
train_104 | What is described in this image? | increase with decreasing cooling rate, as expected. The transition appears to be considerably broadened for the 16 nm film, consistent with the recent work of Nealey and coworkers.25 For the thicker films, no broadening is evident but at low cooling rates, two small peaks appear at temperatures higher than that for the main enthalpy overshoot. This phenomenon has not been previously reported or shown in the literature to the best of our knowledge, and we only observe it for the slowest cooling rates. It is well-known that residual stresses can result in extra peaks in scanning calorimetry, 3-55 and we originally attributed the peaks to residual stress incurred during spin-coating and not relieved by the annealing procedure; however, the peaks are only present in the scans after slow cooling, and they do not evolve or disappear even with 48 h annealing at 160 ℃, as shown in Figure 8a, indicating Figure 8. Flash DSC heating scans for the 71 nm thick film directly spin-cast onto the calorimetric chip: (a) as a function of annealing time that they are not due to unrelaxed stresses from the spincoating process. The peaks may also be attributable to residual thermal stresses that arise due to differences in the thermal expansion coefficients of the back of the chip (silicon oxide) and the polystyrene film. However, thermal stresses should be eliminated above Tg and should accumulate on cooling through T ; hence, thermal stresses are not expected to depend strongly on rate, and if anything, they are expected to be higher for higher rates, which is not the observation here. Furthermore, annealing in the vicinity of the extra peaks, at 145 ℃ for 24 h or at 130 ℃ for 48 h, does not perturb the heat flow curves, as would be expected if the peaks arose from thermal stresses. To was also measured after Apiezon-N grease was applied to the top of the two thickest samples. The resulting heat flow curves are identical to the original curves and to the curves after annealing, as shown in Figure 8b for the 71 nm thick film. | |
train_105 | What is described in this image? | XRD did not show evidence of crystallinity on non-degraded BSPU1, as shown in Fig. 6a, where an amorphous halo with a maximum at 20 = 20° was observed. In the case of BSPU2 (Fig. 6b), two small peaks at 21.3° and 23.7° on top of this amorphous background were identified and related to crystalline domains in the PCL. XRD did not show evidence of crystallinity on non-degraded BSPU1, as shown in Fig. 6a, where an amorphous halo with a maximum at 20 = 20° was observed. In the case of BSPU2 (Fig. 6b), two small peaks at 21.3° and 23.7° on top of this amorphous background were identified and related to crystalline domains in the PCL. to a variable extent and the peaks associated with their crystalline structure were not longer observed (Fig. 6a). A similar behaviour was observed for BSPU2 after acidic and alkaline hydrolysis (Fig. 6b), but degradation in oxidative medium yielded a residue that was difficult to handle (gummy like) and its diffractogram was not obtained. Although it was expected that degradation of the PCL in BSPU1 would lead to a diffractogram similar to a HMDI-BD polyurethane, this was not the case. However, the diffraction patterns of the degraded BSPU1 (see Fig. 6a) showed a (Fig. 6b), but degradation in oxidative medium yielded a residue that was difficult to handle (gummy like) and its diffractogram was not obtained. Although it was expected that degradation of the PCL in BSPU1 would lead to a diffractogram similar to a HMDI-BD polyurethane, this was not the case. However, the diffraction patterns of the degraded BSPU1 (see Fig. 6a) showed a As seen in Fig. 6c, the amorphous structure of Tecoflex® was not affected by any type of degradation. | |
train_106 | What is described in this image? | nanowires in aqueous dispersion. In this case, Tg (~78 °C) of the ~120 nm PS nanowires in aqueous dispersion shows a reduction of ~24.5 ℃ (Tg=Tg, bulk = ~-24.5 ℃) from that of bulk (~102.5 ℃). However, as for the PS nanowires confined in AAO template, no diameter dependence and a slight increase (~3 ℃) in Tg from that of PS bulk are displayed in Fig. 6. Furthermore, the experimental results of DSC characterization are demonstrated in Fig. 7. Compared with PS nanowires confined in AAO template and PS bulk, AC, of PS Fig. 7 DSC curves of PS nanowires in aqueous dispersion, confined in AAO template, and the corresponding PS bulk | |
train_107 | What is described in this image? | The changes of thermal effects with increase annealing time reflect dynamics of bitumen microstructure formation. The bitumen molecules during storage at room temperature after rapid cooling from the melt have time and kinetic conditions for the formation of supramolecular structures. Figure 4 illustrates that these processes are interrelated. Fig. 4 Correlations dependencies between the thermal effects of Table 1 | |
train_108 | What is described in this image? | Fig. 2 is a comparative study of XRD patterns of pure PEO/PVP (a), its complexes with various salt concentrations (b)-(d) and NaBr salt (e). The comparative study reveals that the intensity of all crystalline peaks of PEO decreases gradually, upon the addition of salt to the polymer blend, suggesting a decrease in the degree of crystallinity of the complexes. This could be due to the disruption of the semicrystalline structure of the film by salt. When NaBr dissolves in the polymer host, the interaction between PEO/PVP host matrix and NaBr leads to a decrease of the intermolecular interaction among the polymer chains which reduces the crystalline phase and hence increases the amorphous region. The relative intensities of sharp peaks of PEO at around 19° and 23° in the complexed PEO/PVP blend with 15 wt% NaBr are different from those of pure PEO/PVP blend which indicates that the dopant inhibits the orientation of PEO crystallites preferentially in certain directions [45]. The sharp peaks corresponding to NaBr salt (Fig. 2(e)) observed between 17.27° and 68.61° (PCPDF Card nos. 01-0901, 74-1182 and 72-1539) disappeared in the polymer blend complexes, which indicates the complete dissolution of salt in the polymer matrix [52]. Fig. 2. XRD patterns of PEO/PVP blend films containing NaBr ratios (a) 0 wt8; | |
train_109 | What is described in this image? | The microstructures of the samples aged at 700-900 ℃ are shown in Fig. 15. Aging at these temperatures resulted in precipitation of fine acicular O-phase of different width inside B2-grains. O-phase precipitates can also be found on the B2-grains borders. The chemical composition of the B2-grain borders, measured by EDS, corresponds to Ti2AlNb (Fig. 16). It is characterized by higher Ti and Al content with lower Nb content compared to the B2-matrix. Fig. 15. SEM-images of the Ti-22AA-25Nb samples after aging for 24 h at different temperatures: (8, d) 700 °C; (b, e) 800 °C with the inset to e) showing the area at higher magnification demonstrating the precipitates small size; and (c, f) 900 °C. (Fig. 15, a, d). Increasing the aging temperature to 900 ℃ increased the grain size, and both coarse and fine equiaxed grains can be found in the microstructure (Fig. 15, c, f). After aging the alloy at 1000 ℃ and 1100 °C, there is a higher number of coarse grains with the size of more than 200 µm. (Fig. 15, a, d). Increasing the aging temperature to 900 ℃ increased the grain size, and both coarse and fine equiaxed grains can be found in the microstructure (Fig. 15, c, f). After aging the alloy at 1000 ℃ and 1100 °C, there is a higher number of coarse grains with the size of more than 200 µm. | |
train_110 | What is described in this image? | Fig. 6 displays the densities of the sucrose esters and their corresponding epoxidized products. It shows that the densities of the sucrose esters are below 1.0 g cm-3, but that the densities of their epoxy products are above 1.0 g cm-3. For fully substituted Table 3 Fig. 6 sucrose esters, Fig. 6(a) shows that the density of the sucrose ester increases with the amount of double bonds; Fig. 6(b) shows that the density of epoxidized sucrose ester increases with the amount of epoxide. Sucrose soyate B6 is a partially substituted sucrose ester. It has the highest density of the sucrose esters, due to its higher amount of sucrose (d = 1.587 g cm-3). This has been suppressed after epoxidation, but ESSB6 still has a higher density than ESS. sucrose esters, Fig. 6(a) shows that the density of the sucrose ester increases with the amount of double bonds; Fig. 6(b) shows that the density of epoxidized sucrose ester increases with the amount of epoxide. Sucrose soyate B6 is a partially substituted sucrose ester. It has the highest density of the sucrose esters, due to its higher amount of sucrose (d = 1.587 g cm-3). This has been suppressed after epoxidation, but ESSB6 still has a higher density than ESS. | |
train_111 | What is described in this image? | Figure 2. Chemical formulas of the reactants used for epoxy-anhydride curing. (Figure 2). The prior study showed that the fully substituted ESEFAs contain trace hydroxyls due to the presence of <30 wt % of hexaester and heptaester in the starting sucrose ester resins. Epoxidized sucrose soyate B6 (ESSB6) has additional hydroxyls available because of the partial substitution of the sucrose. Therefore, the presence of hydroxyls needs to be considered in the curing reaction. Additionally, there is trace diacid available in the anhydride | |
train_112 | What is described in this image? | Fig. 3. FT-IR spectra of free curcumin (a), Cur-Lip (b), pure chitosan (c) and CS-Cur-Lip (d). Cur-Lip were determined to investigate the interaction among curcumin, liposome and chitosan. Fig. 3 showed the spectra of different samples. Peaks from 3387 to 3437 cm-1 (-OH and -- NH2 stretching) Lip (Fig. 3b), the peaks at 1738 cm-1 (C=O stretching) and 1507 cm-1 (C-0-C stretching) were regarded as a characteristic peak of lipid acyl chain, which was not found in free curcumin (Fig. 3a). The two new peaks at 1647 cm-1 (amide I, C=0 stretching) and 1554 cm-1 (amide II, -NH2 bending) appeared in pure chitosan Lip (Fig. 3b), the peaks at 1738 cm-1 (C=O stretching) and 1507 cm-1 (C-0-C stretching) were regarded as a characteristic peak of lipid acyl chain, which was not found in free curcumin (Fig. 3a). The two new peaks at 1647 cm-1 (amide I, C=0 stretching) and 1554 cm-1 (amide II, -NH2 bending) appeared in pure chitosan (Fig. 3c) (Grant, Blicker, Piquette, & Allen, 2005). For CS-Cur-Lip (Fig. 3d), the characteristic peak of Cur-Lip at 1738 cm-1 was reappeared, which was not found in Fig. 3c (pure chitosan). Besides, the peak of 1645 cm-1 was shifted from 1647 to 1645 cm-1. It was reasonable to speculate that the structure formation by electrostatic interaction between amine groups of chitosan and phosphoric groups of PC (Fig. 3c) (Grant, Blicker, Piquette, & Allen, 2005). For CS-Cur-Lip (Fig. 3d), the characteristic peak of Cur-Lip at 1738 cm-1 was reappeared, which was not found in Fig. 3c (pure chitosan). Besides, the peak of 1645 cm-1 was shifted from 1647 to 1645 cm-1. It was reasonable to speculate that the structure formation by electrostatic interaction between amine groups of chitosan and phosphoric groups of PC (Fig. 3c) (Grant, Blicker, Piquette, & Allen, 2005). For CS-Cur-Lip (Fig. 3d), the characteristic peak of Cur-Lip at 1738 cm-1 was reappeared, which was not found in Fig. 3c (pure chitosan). Besides, the peak of 1645 cm-1 was shifted from 1647 to 1645 cm-1. It was reasonable to speculate that the structure formation by electrostatic interaction between amine groups of chitosan and phosphoric groups of PC | |
train_113 | What is described in this image? | Figure 5 shows the DSC thermograms of PLANW and related nanocomposites after a cooling step at 10 ℃/min from the molten state. Despite the rigid nature of CNW, the addition of CNW-g- PLA in PLANW results in a noticeable change (decrease) in the glass transition of PLA (ca. 60 ℃), demonstrating that grafted PLA, Figure 5. DSC curves obtained during crystallization under isothermal conditions (at 130 °C) of unfilled PLANW and PLA-grafted CNW-based nanocomposites. | |
train_114 | What is described in this image? | The crystallization volume fraction x at a temperature T during the crystallization can be written as AT/Atotal/ with AT representing the corresponding area of the specific temperature T, while Atotal represents the whole area of the crystallization peak in the DSC curve. According to the DSC traces, the relationship between the crystallization volume fraction x and temperature T of Fe68NbgB23M03 metallic glass for the crystallization event at different heating rates is shown in Figure 5. The slope of the x-T curves denotes the crystallization rate at a stationary heating rate. The x-T curves display a representative S-type shape. At the beginning and end of the x-T curve, the crystallization rate is small, and when x is in the range of 10-80%, the crystallization rate is large. As the heating rate increases, the x-T curve shifts to the right, revealing a typical thermal drive process. Figure 5. The x-T curves of the Fe&NboB23M03 glassy alloys under various heating rates. | |
train_115 | What is described in this image? | Variation in the value of Tg of the PPy–epoxy resin Figure 4. cribed well by Equation (1) with pc = 11 wt .- %. At higher PPy contents, ode reaches a value of 1 × 10-4 S . cm-1 at 20 wt .- %. Figure 4 shows the dependence of the DSC Tg on the weight fraction of PPy. T increases linearly with PPy wt .- % as expected in polymer blends where T obeys the Fox equation: | |
train_116 | What is described in this image? | Fig. 5 (A) Indexed SAED pattern for W-doped VO2 nanobelts along the patterns shown in Fig. 5. The fringe spacings observed in Fig. 5B patterns shown in Fig. 5. The fringe spacings observed in Fig. 5B | |
train_117 | What is described in this image? | Fig. 8 shows the results of the dew-point measurements. | |
train_118 | What is described in this image? | Fig. 1 shows TEM micrographs of samples II and III. Dark regions are assigned to the SEBS particles in which the characteristic domain structure of the block copolymer is seen (not so clear in Fig. 1 but obvious in Fig. 9). Average particle size in the ternary Fig. 9. TEM micrograph of PLA-h/PC/SEBS/EGMA = 60/20/15/5; magnified from Fig. 6a. Fig. 9 is a magnified TEM micrograph of Fig. 6a. Between the elongated PC particle and PLA matrix, a grey boundary is seen. The boundary may be assigned to a multiblock or random copolymer formed by the exchange reactions between PLA and PC during melt mixing. The copolymer is expected to enhance the interfacial adhesive strength. The formation of such copolymers is supported by DMA data in Fig. 10. | |
train_119 | What is described in this image? | From TMDSC measurements during isothermal crystallization of iPS it is known that the rigid amorphous fraction is formed during isothermal crystallization [78]. On the other hand fast scanning data (Fig. 13) indicate the beginning of a continuous melting-recrystallization-remelting process in the vicinity of the annealing peak [125]. Such a continuous melting-recrystallization-remelting process certainly requires mobility in the neighborhood of the molten crystals and, consequently, devitrification of the rigid amorphous fraction. This is further supported by the observed step in heat capacity at the annealing peak. By making use of these arguments construction of baseline heat capacity also becomes possible. Above glass transition (110-140°C) baseline heat capacity equals measured heat capacity and takes into account the existence of a rigid amorphous fraction. At the annealing peak a step-like increase in heat capacity towards the expected value from a two phase model is assumed to describe devitrification of the rigid amorphous fraction. Such baseline heat capacity is indicated in Fig. 23. Using baseline heat capacity from Fig. 23 and Eqs. 24 and 25 allows determination of all three fractions of a semicrystalline polymer as a function of temperature. The results for the mobile amorphous, rigid amorphous, and crystalline fractions are shown in Fig. 24. Fig. 23 Measured and baseline heat capacity for iPS isothermally crystallized at 140°C for 12 h as a function of temperature for heating at 10 Kmin-1. For details see text | |
train_120 | What is described in this image? | The mass loss curve of FS is shown in Fig. 3. There are three well-resolved effects of mass loss on it, so we can use them to clarify the composition of the compound. As it can be seen from TGA curve, these effects take place in the temperature ranges of 300–500, 500–900 and 900–1050 K. The mass loss in the first step is (12.30±0.10)%, in the second step (17.91±0.17)%, and in the weak last one (0.85±0.13)% (P=0.95, n=7). The total mass loss is Fig. 3. Results of thermal analysis of FS. The shape of DSC curve (Fig. 3) agrees with the mass loss curve. | |
train_121 | What is described in this image? | techniques, 66 see Appendix 6.1 for details. The T-junction and the microfluidic channels were arranged according to the geometry of Garstecki et al.64 All channels were 25 ± 5 µm in height. The channel of the aqueous phase was close to half the width (55 ± 5 um) of the organic phase channel (107 ± 5 um). Syringe pumps (neMESYS14,1; Cetoni; Syringes: Hamilton TLLX, 25 µL) were used to control the flow rates of the organic and aqueous phases. The syringes were connected to the microfluidic channels by means of interconnection-blocks (5 in Fig. 1b; see also Fig. 8 in Appendix 6.1 for details). After the droplets were produced at the T-junction, they passed a second interconnection-block and an outlet tube for collection and further off-chip characterization. Fig. 8 Photograph of the microfluidic device used in this study. The inset shows the side view of the channels in the interconnection blocks attached to the device. Plasma oxidation of PDMS results in hydrophilic surfaces and was used as a means to connect the microfluidic structure to a cleaned silicon wafer, because upon contact of the two surfaces, inter-surface covalent bonds form.79,80 Interconnection-blocks (IBs) were developed according to Sabourin et al.84 to allow the connection between the syringe pumps and the microfluidic structure (Fig. 8) at the two inlets. A third interconnection-block connected the microfluidic structure with the outlet tubing. The IBs were also made from PDMS (same composition as above) which was cured in an aluminium mold. The channels of the interconnection-blocks were imprinted into the PDMS using glass fibres (0.25 mm in diameter) and plastic tubes (0.70 mm in diameter) as molds. Both, the glass fibres and tubes were pulled out of the PDMS after curing (Fig. 8). One side of the interconnection-blocks then contained channels which opened to a diameter of 0.70 mm to be connected to the pumps. The tubings (outer diameter of 0.79 mm) of the syringe pumps were plugged to a tight fit into this side of the interconnection-blocks. The channels inside the interconnection-blocks narrowed to a diameter of 0.25 mm. These channels ended in a hemisphere | |
train_122 | What is described in this image? | and after different post-treatment is shown in Fig. 18. | |
train_123 | What is described in this image? | where Q is the heat flow rate, AHm is the enthalpy of fusion, dT/dt is the temperature scanning rate, mice is the mass of ice, m3q is the mass of water, and Cpice and Cpaq are heat capacities of ice and water, respectively. A two-phase envelope of ice-salt water is shown in figure 8 [15]. Using the inverse-lever rule, the mass of ice can be written as a function of temperature, so the total mass of the sample is given by mlot = mace + mag, and the mass is distributed between salt water and ice by where wed(T) is the equilibrium salt water mass fraction at a given temperature, taken from figure 8. The number in the numerator is the prepared sample mass fraction, which in this case is | |
train_124 | What is described in this image? | Shown in Figure 1 is a circuit board with only the connections laid out, no components attached. While some connections can be seen topically on the green substrate, other connections are within or underneath the board as the connections of various components cannot cross. The shapes and lines on the circuit board in Figure 1 represent the locations where the designated electronic components need to be connected to produce a functional circuit board. Shown in Figure 1 is a circuit board with only the connections laid out, no components attached. While some connections can be seen topically on the green substrate, other connections are within or underneath the board as the connections of various components cannot cross. The shapes and lines on the circuit board in Figure 1 represent the locations where the designated electronic components need to be connected to produce a functional circuit board. Figure 1: Unpopulated circuit board shown with only connections laid (Upton) In SI Figure 1, the DSC results for the material are shown with no hardener added. Since the hardener was not added there is no reaction taking place. If the small initial peak shown in experimental data was a system response, the binder/filler itself, or the instrument, it would be shown here. Since no response can be seen here it can be surmised that the initial reaction is a part of the material curing itself. SI Figure 1: DSC non-isothermal experiment with no hardener added to ACA | |
train_125 | What is described in this image? | Annealing time has little effect on Tg, Tx and Tp in the two bulk metallic glasses (Fig. 8(a), (b)). However, when the annealing time is long enough, Tg increases while Tx is decreasing. Wang et al. [49] studied the structural relaxation in Pd40Cu30Ni10Pd20 bulk metallic glass and proposed that this evolution observed when the annealing time is too long is due to new defects on the interfaces between the solid-liquid regions in the bulk metallic glass. Wang et al. [45] proposed that in such conditions partial decomposition has occurred in the residual amorphous matrix. In other words, compared with as-cast alloys, crystallization nuclei may be created during a long annealing time. These assumptions are fairly difficult Meanwhile, it can be seen from Fig. 8(c) that ΔCp increases with increasing the annealing time in Cug6Zr45A17Y2 and Z155CU30Ni5A110 bulk metallic glasses and then tend to equilibrium. This phenomenon corresponds to a progressive evolution of the free volume or of the quasi-point defect concentration towards the equilibrium Fig. 8. Thermal parameters: Tg, Tp, Ip, Ip, in Zr55Cu30NigAl10 and Cu46Zr45Al312 bulk metallic glasses. (a) Tg, Tg in Cu62r45Al7Y2 annealed at 674 K after various annealing time ta: (b) Tg, Tx, Tp in Zr55Cu30Ni5Al10 annealed at 659 K during various annealing time t .: (c) glass transition peak height (ΔCn) in the bulk metallic glasses with different annealing times. | |
train_126 | What is described in this image? | C2A3, CA, CA2, CAg, and aluminum and calcium oxides, prepared by the same process for comparison, are shown in Fig. 3. The spray-dried aluminum nitrate is decomposed between 100° and 350°C, with two maxima for the weight loss rate, determined from Fig. 3. | |
train_127 | What is described in this image? | dissolved in P111i4FSI (0.5, 3.2 and 3.8 mol kg-1) at room temperature using a Ni working electrode are presented in Fig. 9. Fig. 9 Linear sweep voltammograms (1st cycle) for neat P111;4FSI and solutions of 0.5, 3.2 and 3.8 mol kg-4 LiFSI in P11114FSI at a Ni working electrode with a potential sweep rate of 20 mV s-1 at 25 °C. | |
train_128 | What is described in this image? | Fig. 2 DSC measured transitions Figure 2 summarizes typical material transitions (properties) measured by DSC and indicates whether each is reversing or nonreversing. Note that several transitions, particularly polymer melting, contain both reversing and nonreversing characteristics. MDSCTM facilitates the separation of reversing and nonreversing transitions. Fig. 2 DSC measured transitions Figure 2 summarizes typical material transitions (properties) measured by DSC and indicates whether each is reversing or nonreversing. Note that several transitions, particularly polymer melting, contain both reversing and nonreversing characteristics. MDSCTM facilitates the separation of reversing and nonreversing transitions. | |
train_129 | What is described in this image? | Fig. 4. The melting DSC curves of the SA, CPCM 1, CPCM 2 and CPCM 3. The DSC results of SA, CPCM 1, CPCM 2 and CPCM 3 are presented in Fig. 4, Fig. 5 and Table 1. The latent heat data of the composites are compared with the data calculated from Eq. (1), and shown in Table 2. ΔΗραΜ represents the calculated latent heat of the composites, the value of n is the mass percentage of the SA in the composites, and AH5A represents the latent heat of the SA as measured by the DSC. The experimental values of latent heat accord well with the calculated values with differences less than ±5%. | |
train_130 | What is described in this image? | The effect of increase in drug loading on the no is illustrated in Fig. 6. The trends observed for changes in no with the increase in drug loading could be interpreted based on the Tm and consequently the state of the drug in the polymer at the softening temperature. For instance, low melting IND was miscible with the polymers at the softening temperatures of the PMs and depicted concentration dependent decrease in 10 for almost all the polymers (Fig. 6a) due to dissolution of the drug in the polymer at those temperatures. However, GSF with very high Tm was dispersed as crystalline drug in the polymers at the softening temperatures of the PMs and exhibited concentration dependent increase in ηo for all the polymers (Fig. 6b). As shown in Fig. 6c and d, ITZ with moderately high Tm was miscible with Eudragit L-100-55, Eudragit L-100, and Pharmacoat 603 at the softening temperatures and depicted concentration dependent decrease in ης. However, it was dispersed as crystalline drug in 70:30 ratios with HPMCAS-LF, HPMCAS-MF, and Kollidon VA 64 at the softening temperatures and exhibited higher higher drug loading would be difficult for IND and GSF due to very low and very high 10, respectively (Table 2a and c). On the other hand, it could be possible to produce HMEs of ITZ with some of the polymers such as Eudragit L-100-55, HPMCAS-LF, and HPM- (Fig. 6a) due to dissolution of the drug in the polymer at those temperatures. However, GSF with very high Tm was dispersed as crystalline drug in the polymers at the softening temperatures of the PMs and exhibited concentration dependent increase in ηo for all the polymers (Fig. 6b). As shown in Fig. 6c and d, ITZ with moderately high Tm was miscible with Eudragit L-100-55, Eudragit L-100, and Pharmacoat 603 at the softening temperatures and depicted concentration dependent decrease in ης. However, it was dispersed as crystalline drug in 70:30 ratios with HPMCAS-LF, HPMCAS-MF, and Kollidon VA 64 at the softening temperatures and exhibited higher higher drug loading would be difficult for IND and GSF due to very low and very high 10, respectively (Table 2a and c). On the other hand, it could be possible to produce HMEs of ITZ with some of the polymers such as Eudragit L-100-55, HPMCAS-LF, and HPM- (Fig. 6a) due to dissolution of the drug in the polymer at those temperatures. However, GSF with very high Tm was dispersed as crystalline drug in the polymers at the softening temperatures of the PMs and exhibited concentration dependent increase in ηo for all the polymers (Fig. 6b). As shown in Fig. 6c and d, ITZ with moderately high Tm was miscible with Eudragit L-100-55, Eudragit L-100, and Pharmacoat 603 at the softening temperatures and depicted concentration dependent decrease in ης. However, it was dispersed as crystalline drug in 70:30 ratios with HPMCAS-LF, HPMCAS-MF, and Kollidon VA 64 at the softening temperatures and exhibited higher higher drug loading would be difficult for IND and GSF due to very low and very high 10, respectively (Table 2a and c). On the other hand, it could be possible to produce HMEs of ITZ with some of the polymers such as Eudragit L-100-55, HPMCAS-LF, and HPM- | |
train_131 | What is described in this image? | content, which suggested that TAP acts not only as crosslinkers but also as chain extenders, similar to other covalent cross-linked systems reported.50 The schematic illustration for the structure of thermoset shape-memory polyimides is manifested as Figure 6. Figure 6. Schematic illustration of thermoset shape-memory polyimide. The black lines represents the polyimide chains; the red and green Y-type symbols represents TAP acting as cross-linkers and chain extenders, respectively. 222, and 212 °C, respectively. 3,27,28 The chemical structures of the above-mentioned shape memory polyimide samples are illustrated in the Supporting Information (Figure 6S). For dianhydrides, ODPA possess one ether linkage and BPADA | |
train_132 | What is described in this image? | Fig. 5 shows the temperature program of the ultrafast DSC This can be repeatedly confirmed from the cooling process of Fig. 5, as shown in Fig. 9. During the cooling process after heating at a rate of 100 °C s-1 (see Fig. 9(h)), the crystallization temperature reduced significantly. Further, the crystallization enthalpy (AHc) The zep melting–melting without the occurrence of cold crystallization, reorganization, and superheating during the heating process-is discussed in this section. For the preparation of samples with different crystalline states, the measurement method shown in Fig. 5 was employed with different cooling rates from the molten state (i.e., -5000 °C s=1 and -7500 °C s-1). (see the measurement method in Fig. 5). It was confirmed that Tc depends on the cooling rate from the molten state as shown here: | |
train_133 | What is described in this image? | Fig. 3 DSC curves of steel 1 obtained during heating (a) and cooling (b) with the heating/ cooling rates of 5 and 20 ℃ min-1; characteristic temperatures: Ty->8 temperature of o-ferrite formation, TPER | |
train_134 | What is described in this image? | 2.7. Tensile and Welding Properties. Figure 7 shows the stress-strain curves of the cured epoxies. All the samples Figure 7. Stress=strain curves of DER-1, TEP-1, and TEP-2. The picture on the right side is the digital photo of the test specimens. | |
train_135 | What is described in this image? | 3.2.2 1H-NMR. Fig. 3 displays the 1H-NMR spectra of SSF and ESSF. The spectrum of SSF shows the characteristic peaks of protons on double bonds (-CH=CH-) at 5.21-5.50 ppm, the peaks of protons on the carbons between double bonds (-CH=CH-CH2-CH=CH-) at 2.72-2.83 ppm, and the peaks of protons on the carbons next to double bonds (-CH2-CH=CH-) at 1.95-2.10 ppm. In the spectrum of ESSF, | |
train_136 | What is described in this image? | Figure 3. Indium calibration run | |
train_137 | What is described in this image? | Before compression moulding, multilayer 0/90 bidirectional hybrid yarn prepregs were prepared by winding the hybrid yarn around a 19 × 19-cm steel rectangular frame (Fig. 2). A 0/90 bidirectional layup of the prepreg was chosen, due to the ease of the winding technique. Each prepreg had 12 layers of wound yarns, to achieve a composite thickness of about 1–3 mm. The prepreg mats were first put in a vacuum chamber (0.9 mbar; 20 °C) for at least 18 h, to dry before the compression moulding. The prepreg was covered with a Teflon sheet to prevent sticking of the matrix to the surface of the mould before being placed into a pre-heated steel mould with a 20 × 20-cm square cavity, and 10 mm depth. | |
train_138 | What is described in this image? | (Scheme 2). The structure of HODEAz (8) was confirmed by FTIR and 13C NMR spectroscopy. The FTIR spectrum shows a strong absorption band at 2133 cm-1 due to asymmetric stretching vibration of azide group (N3) and also a shift of the carbonyl group band from 1707 to 1720 cm-1 due to the formation of a more electron withdrawing azide group (Figure 3). In addition, a band due to the C=C-H stretching vibration appeared at 3008 cm-1. In the 1H NMR spectrum of HODEAz (8), a triplet peak of the methylene group attached to an azide group (CH2-CON3) appears at 2.31 ppm and vinylic protons (CH=CH) appear at 5.2-5.60 ppm (Figure 4). 13C NMR (Figure 4). 13C NMR spectrum shows an urethane carbonyl function at 156.57 ppm confirming self-condensation. | |
train_139 | What is described in this image? | The thermal properties for pure octadecane are given in different references which are collected by the National Institute of Standards (NIST) [24]. Table 2 shows the values used in this paper as reference. Fig. 1 shows the enthalpy of octadecane in function of temperature built with the reference values. Fig. 1. Enthalpy vs. temperature curve of octadecane built from the reference values (NIST values) | |
train_140 | What is described in this image? | Tack showed an even stronger dependence on CT at both room temperature (23°C) and cold temperature (4℃) shown in Figure 2. At room temperature the tack was poor (i.e., maximum value) for CT = - 8°C (265 K) and good for CT s Figure 2 Tack as a function of calculated Tg-Dsc (using DSC component values and the Fox equation). | |
train_141 | What is described in this image? | Lost heat is a systematic error that is addressed with calibration: i) for pan-style DSCs if and only if the carrier gas, heating rate, detector, sample container mass and thermal properties, and approximate sample mass are all consistent, and ii) Tian-Calvet DSCs if and only if heating rate, detector, sample container mass and thermal properties, and approximate sample mass are all consistent. A higher efficiency ratio increases the detector signal, thereby reducing the detection limit of the sensor. Crucibles of the heat-flux DSC rest on a thin plate. The efficiency ratio is directly proportional to the plate thickness, which varies between 0.010.1 mm (Figure 11). At ambient temperature, the efficiency ratio reaches 50 % and drops to 30 % at 600 ℃ for the 0.05 mm. Figure 11. Heat signal efficiency (%) of a two-dimensional heat-flux DSC probe as a function of temperature built with a 0.01 mm (circle), a 0.05 mm (triangle), and a 0.1 mm (square) thick plate (source: SETARAM). | |
train_142 | What is described in this image? | Fig. 12. Effect of cold deformation on the TDS spectrum of pure iron. steel. The corresponding TDS spectra are shown in Fig. 12. The graphs are only shown up to 300 ℃ because there were no high temperature peaks present in the spectrum. The only peak observed was the low intensity peak detected at about 90 ℃. The height of the peak was nearly identical for all samples, and a minor shift of the peak temperature by a few degrees with increasing deformation was observed. | |
train_143 | What is described in this image? | Fig. 7 shows the TGA curves of PVDF, PEG1000, and e-spun PEG1000/PVDF composite nanofibers. It shows that PEG1000 degraded completely at 435 °C, while PVDF began its degradation at 470 °C. The e-spun PEG1000/PVDF composite nanofibers degraded in two stages: the first stage was below 440 °C and the second one was above 440 °C. The first stage was ascribed to the thermal degradation of PEG1000, and the latter one, to thermal degradation of PVDF in the e-spun PEG1000/PVDF composite nanofibers. The weight loss of e-spun PEG1000/PVDF composite nanofibers below 440 ℃ was around 25 wt%, which is near the amount of PEG1000 in the e-spun composite nanofibers. The results of the DSC analysis and TGA, as shown in Fig. 7 and Table 4, indicate that the PEG content in PEG/PVDF core/shell composite nanofibers fabricated by melt coaxial electrospinning was higher than that in the fibers fabricated by solution coaxial electrospinning reported in our previous research (around 20 wt%) [21]. The obtained core/shell nanofiber mat contained 42.5 wt% of 4000 Da PEG in its core, resulting in the highest efficiency of energy absorbing (68 J/g) and releasing (62 J/g) Fig. 7 shows the TGA curves of PVDF, PEG1000, and e-spun PEG1000/PVDF composite nanofibers. It shows that PEG1000 degraded completely at 435 °C, while PVDF began its degradation at 470 °C. The e-spun PEG1000/PVDF composite nanofibers degraded in two stages: the first stage was below 440 °C and the second one was above 440 °C. The first stage was ascribed to the thermal degradation of PEG1000, and the latter one, to thermal degradation of PVDF in the e-spun PEG1000/PVDF composite nanofibers. The weight loss of e-spun PEG1000/PVDF composite nanofibers below 440 ℃ was around 25 wt%, which is near the amount of PEG1000 in the e-spun composite nanofibers. The results of the DSC analysis and TGA, as shown in Fig. 7 and Table 4, indicate that the PEG content in PEG/PVDF core/shell composite nanofibers fabricated by melt coaxial electrospinning was higher than that in the fibers fabricated by solution coaxial electrospinning reported in our previous research (around 20 wt%) [21]. The obtained core/shell nanofiber mat contained 42.5 wt% of 4000 Da PEG in its core, resulting in the highest efficiency of energy absorbing (68 J/g) and releasing (62 J/g) Fig. 7. TG curves of (a) PVDF, (b) PEG1000 and (c) e-spun PEG1000/PVDF | |
train_144 | What is described in this image? | Figure 12 Plots of loss modulus versus angular frequency for the PLA and PLA/MBS blends. Figure 12 displays the relationship between loss modulus and angular frequency of the PLA/MBS | |
train_145 | What is described in this image? | The ratio of these rates results in the diffusion factor DF (Eq. (5)). The evolution with reaction time of the heat flow diffusion factor DF and the heat capacity mobility factor DF* is shown in Fig. 6. Both factors, originating from two different experimental quantities, give quantitatively the same evolution and almost coincide. Fig. 6. The cure of an epoxy-amine at 70℃: comparison of the mobility factor based on heat capacity | |
train_146 | What is described in this image? | Effect of operating temperature. Effect of operating temperature on permeability and selectivity of MMMs were studied from 25 ℃ to 65 °C at the pressure of 8 bar. Fig. 15 shows that permeability of all the tested gases increases with temperature. The reason can be deduced by looking at Arrhenius types of equation that are used to describe temperature dependency of transport properties through As it can be seen from Fig. 15, the slope of increasing permeation for N2 and CO2 after 45 °C, especially for MMM at higher loadings, is sharper than that at lower temperatures. Also, unlike at low temperatures that permeation for membranes with 20 wt% and 30 wt% zeolite, was almost similar and slight particle agglomeration or polymer chain rigidification was suggested as the probable reason, at higher temperatures permeation through membrane with 30 wt% loading is higher than that of 20 wt%. This proves reduction in chain rigidification and improvement in polymer chain mobility around particles that makes them more active [8]. Fig. 15 (red graphs) shows the effect of temperature on CO2/N2 and CO2/CH4 ideal selectivity at 8 bar and various SAPO-34 zeolite loading. As shown in Fig. 15, CO2 selectivity over CH4 and N2 decreases with rising temperature. This is because of more increment in permeation of CH4 and N2 in comparison with CO2, which was discussed above. Fig. 15 (red graphs) shows the effect of temperature on CO2/N2 and CO2/CH4 ideal selectivity at 8 bar and various SAPO-34 zeolite loading. As shown in Fig. 15, CO2 selectivity over CH4 and N2 decreases with rising temperature. This is because of more increment in permeation of CH4 and N2 in comparison with CO2, which was discussed above. | |
train_147 | What is described in this image? | The plot of the heat of fusion values, as a function of the degree of crystallinity was constructed (Fig. 6) and extrapolation to 100% Fig. 6. Plot of the heat of fusion vs. degree of crystallinity for the polyesters under study. | |
train_148 | What is described in this image? | As said before, different samples of graphite/salt composites have been elaborated by uni-axial cold-compression. Graphite amount within the samples ranges from 5 to 20%wt. Each sample has been cycled at least 10 times in the DSC. Fig. 3 shows the Fig. 3. Measured compensation flux when heating (positive values) or cooling (negative values) a sample with 15% wt of graphite amount (10 cycles at 5 °C/min). | |
train_149 | What is described in this image? | The effect of glycerol and oil in chitosan and galactomannan films was initially evaluated by FTIR analyses. Fig. 1a shows the FTIR spectra of the chitosan (CH) films containing 0, 0.5, 1.25 and 2.0% of glycerol (Gly). The broad band ranging between 3500 and 3100 cm™ is attributed to O-H stretching vibration that overlaps the N-H stretching vibration in the same region. The broad band between 2800 and 3000 cm-1 is attributed to C-H stretching vibration. The peak at 1574 cm-1 was due to the N-H beading Fig. 1. FTIR spectra of chitosan films for increasing glycerol (a) and oil (b) concentrations. Fig. 1b shows FTIR spectra of chitosan films for increasing oil concentrations. FTIR spectra of chitosan films with oil also show a high and more intense number of peaks in the frequency range between 2800 and 3100 cm=1. By the deconvolution of FTIR band ranging between 2500 and 3500 cm=1 a different number of peaks appear for chitosan films without and with oil. These results are presented in Table 3 in the Supplementary data, where two new peaks appear when oil is added to chitosan films. The most relevant peak, ca. 2925 cm=1, can be related with the symmetric and asymmetric stretching vibration of the aliphatic group (CH2) | |
train_150 | What is described in this image? | By optimizing the synthesis conditions, the PMMA/paraffin microcapsule particles were finally obtained. However, the particles were easily agglomerated into lumps and no microcapsules were obtained under condition (a), as shown in Fig. 1a. It was thought that the poor stability of the reactants emulsion was probably the main factor causing the formation of aggregation. This agglomeration can be avoided if the emulsion is stirred at the speed of 10 krpm with a homogenizer followed by mechanical stirring during the emulsification process. Thus, a small amount of microcapsules can be obtained using the synthesis approach under condition (b), as shown in Fig. 1b. When the stirring duration of using the homogenizer was elongated to 3 min, the products of proper microcapsules were formed, as shown in Fig. 1c, which indicates that most of the microcapsules are proper spheres in micron-scale with smooth and compact surface. The diameter of the spheres ranges from 0.5 to 2 um. However, further increase in the homogenization stirring time to 5 min does This agglomeration can be avoided if the emulsion is stirred at the speed of 10 krpm with a homogenizer followed by mechanical stirring during the emulsification process. Thus, a small amount of microcapsules can be obtained using the synthesis approach under condition (b), as shown in Fig. 1b. When the stirring duration of using the homogenizer was elongated to 3 min, the products of proper microcapsules were formed, as shown in Fig. 1c, which indicates that most of the microcapsules are proper spheres in micron-scale with smooth and compact surface. The diameter of the spheres ranges from 0.5 to 2 um. However, further increase in the homogenization stirring time to 5 min does Fig. 1. The SEM images of PMMA/paraffin microcapsules prepared under various conditions, i.e. (a) mechanical stirring at 600 rpm for 30 min only; (b) mechanical stirring at 600 rpm for 30 min and at 10 k rpm using a homogenizer for 1 min; not result in any improvement of the product yield, and some microcapsules are broken and attached to each other, as shown in Fig. 1d. Therefore, condition (c), i.e. mechanical stirring at 600 rpm for 30 min and at 10 k rpm using a homogenizer for 3 min, was employed as the optimum synthesis condition in this study. The latent heat (enthalpy) in heating process (AHm) and the peak temperature of melting (Tm) of the paraffin are 165.01 Jg-1 and 33.6 ℃, respectively. The paraffin phase in microcapsules of sample 1c changes from solid to liquid between 17 and 33 ℃ with a AHm of 101 J g-1 and Tm of 28 °C. Paraffin content in microcapsules is further calculated based on ΔΗΜ, by assuming that the microencapsulation does not affect the AHm of core materials [27]. Accordingly, the content of paraffin in microcapsules of sample 1c is 61.2 wt%. The AHm of samples 1a, b and d are 21.22, 31.07 and 75.95 Jg-1, respectively. These ΔHm values are in accordance with the differences in the amounts of microcapsules observed by SEM in Fig. 1 for each sample. Although there are no microcapsules found by SEM, sample 1a still shows a AHm of 21.22 J g-1. The latent heat was probably induced by the capillary pores in the aggregation, which could constrain some paraffin. Compared with the MEPCMs with PMMA shell prepared by some researchers previously [10], the content of paraffin of microcapsules prepared in this paper increases by more than 118%. | |
train_151 | What is described in this image? | Fig. 11. Effect of frequency on Tan d of epoxy (from left to right in transition interval: 0.1, 0.5, 1, 5, 10, 50, 100 Hz). Table 3 Effect of frequency on T of epoxy | |
train_152 | What is described in this image? | As shown in Fig. 2 the first intense peak in all Group A samples emerged at around 140 cm-1, followed by a very weak shoulder at 200 cm ¯ 1. The first intense peak in all Group A samples emerged at around 140 cm-1, followed by a very weak shoulder at 200 cm-1. These peaks confirm the existence of Bi3+ cations in [BiO3] and Fig. 2. The Raman spectra of 30 Bi group. | |
train_153 | What is described in this image? | Additionally, the lithium ion transference number (tij+) had been determined by combining the measurements of impedance spectra and DC polarization at 60 °C. Results are shown in Fig. 5 and are summarized in Table 2 for both pure PEO and the composite electrolytes with 7.5 wt.% LLZO content. The value of the for the composite electrolytes with 7.5 wt.% LLZO content is 0.207 and 0.159 for the PEO-only electrolyte. This enhancement could be explained by the fact that LLZO is an active lithium ion conductor in which the transport number is unity. Consequently, the incorporation of LLZO powder as inorganic filler in the PEO matrix not only improves the ionic conductivity but also achieved a positive effect on the electrochemical window and lithium ion transference number. The combination of these advantageous changes in properties make this a promising electrolyte for application to nextgeneration all-solid-state batteries. The interfacial behavior between a lithium electrode and the solid electrolyte also has been investigated with the symmetrical cell at a current density of 0.2 mAh·cm™2 under 60 °C. As shown in Fig. 5c and d, the cell with PEO-only solid polymer electrolyte exhibits instability with some short circuiting during operation. This mainly comes from the formation of lithium dendrites and poor electrochemical properties of pure PEO. Nevertheless, when the solid electrolyte is replaced by the composite electrolyte the cells are much more stable and exhibit superior voltage profiles. These results indicate that inorganic LLZO particles in the PEO matrix can reinforce electrochemical stability and ionic conductivity of SPEs and establish stable interfaces with a lithium metal anode. Additionally, the lithium ion transference number (tij+) had been determined by combining the measurements of impedance spectra and DC polarization at 60 °C. Results are shown in Fig. 5 and are summarized in Table 2 for both pure PEO and the composite electrolytes with 7.5 wt.% LLZO content. The value of the for the composite electrolytes with 7.5 wt.% LLZO content is 0.207 and 0.159 for the PEO-only electrolyte. This enhancement could be explained by the fact that LLZO is an active lithium ion conductor in which the transport number is unity. Consequently, the incorporation of LLZO powder as inorganic filler in the PEO matrix not only improves the ionic conductivity but also achieved a positive effect on the electrochemical window and lithium ion transference number. The combination of these advantageous changes in properties make this a promising electrolyte for application to nextgeneration all-solid-state batteries. The interfacial behavior between a lithium electrode and the solid electrolyte also has been investigated with the symmetrical cell at a current density of 0.2 mAh·cm™2 under 60 °C. As shown in Fig. 5c and d, the cell with PEO-only solid polymer electrolyte exhibits instability with some short circuiting during operation. This mainly comes from the formation of lithium dendrites and poor electrochemical properties of pure PEO. Nevertheless, when the solid electrolyte is replaced by the composite electrolyte the cells are much more stable and exhibit superior voltage profiles. These results indicate that inorganic LLZO particles in the PEO matrix can reinforce electrochemical stability and ionic conductivity of SPEs and establish stable interfaces with a lithium metal anode. | |
train_154 | What is described in this image? | This appears at first sight to be a significant advance on the capabilities of conventional DSC. However, one must bear in mind certain assumptions that are inherently made. First, it is assumed that the average, for example, of heating at 7.3 K min- and cooling at -5.3 K min-1 will have exactly the same effect as heating at 1 K min-1. This will be strictly true only if the response of the heat flow is linearly proportional to the heating rate and if the sample is able to follow the programmed heating/cooling rate. Taking each of these in turn, a linear response might be valid in temperature regimes distant from transitions, where no structural changes are taking place, such that the modulated heat flow is bounded by upper and lower limits of mcpqmax and mcpqmin, respectively; this is the approach involved in the "envelope analysis" offered as part of the Mettler Toledo software, and is illustrated in Fig. 4. Within a transition, however, where structural changes are occurring leading to complex time and temperature dependencies for the heat capacity, the assumption of a linear response is more difficult to justify. Under such circumstances, one could anticipate results which depend on the choice of experimental variables Second, the ability, or otherwise, of the sample to follow the heating rate modulations is also important. | |
train_155 | What is described in this image? | To further study the effect of these plasticizers on the transparency of the PLA. The UV-visible light transmittance of treated and plasticized PLA with TEC and ATBC were measured as shows in Figure 8a and Figure 8b. To further study the effect of these plasticizers on the transparency of the PLA. The UV-visible light transmittance of treated and plasticized PLA with TEC and ATBC were measured as shows in Figure 8a and Figure 8b. Figure 8. UV- Visible spectra of treated PLA and plasticized PLA with: (a) TEC; (b) ATBC at various concentrations. | |
train_156 | What is described in this image? | Fig. 9 shows the plot of ln(M /Mo) versus T, for the CH2 carbon atom at 8 = 45 ppm for all compositions. The experimental data give a single exponential decay function. | |
train_157 | What is described in this image? | The values obtained (127-5 and 127-9℃) were similar to those obtained by DSC (121-3 and 123-1ºC) but the transitions were clearer (Figure 3). Figure 3. | |
train_158 | What is described in this image? | alloy, a thermal analysis of the sample produced at 55 J/mm3 VED was conducted by way of DSC. DSC-analysis was carried out at 5 ℃/min heating rate up to 1400 ℃. Two-phase transformation can be found on the obtained DSC-curve (Fig. 10, a): 1) an exothermal peak at 600-650 ℃ temperature range corresponding to the decomposition of martensitic x - phase into (a + ß)-phases; 2) a broad endothermic peak at 850-950 °C temperature range corresponding to a->B/B2 transition. Martensitic o'-phase might be present in the as-is alloy as a result of fast cooling of material volumes in which Ti, Al and small amounts of Nb were melted during the SLM process [26]. Areas with chemical inhomogeneities might be formed during the SLM. In some of the volumes within the sample, Al content was sufficient enough to form a-phase, but Nb content was too low to stabilize ß-phase. Due to a low amount of the martensitic phase, it was not detected on XRD-patterns. The second 5 microstructure was also subjected to DSC-analysis at 5 ℃/min heating rate. The obtained DSC-curve (Fig. 10, b) significantly differs from the curve for the as-is sample. There are two exothermal (at 860 ℃ and 1069 °C) and two endothermal peaks (at 978 °C and 1238 °C) found on the DSC-curve. The first DSC-peak at 860 ℃ corresponds to O->B2 transition. The endothermal peak at 978 ℃ corresponds to the formation of a2-phase. The exothermal peak at 1069 ℃ corresponds to the dissolution of O-phase. The peak at 1238 ℃ corresponds to a2-phase dissolution and transition to a single-phase B2-region. The observed DSC-curve peaks correspond to typical phase transitions for Ti-22Al-25Nb alloy [29,30]. However, transition temperatures are shifted towards higher temperatures, which might be the result of chemical composition difference in the sample compared to the initial powder mixture resulting in decreased Al content. Therefore, Nb content in the sample is relatively higher than in the powder mixture leading to increased temperature stability of B2-phase [31]. | |
train_159 | What is described in this image? | spectrum (see Fig. 1(a)). The determination of the kinetic parameters of this mobility give a value En = 45 kJ mol -1, not far from the value of the zero entropy line (ZEL) [41,42] (for Tmax = 173.2 K, E2ZEL = 37RTmax = 53 kJ mol-1). thermogram. Above this temperature, however, a new mobility appears as shown in Fig. 1(b) where partial polarization peaks with polarization temperature from Tp = 313 K (maximum intensity temperature observed Tmax = 321 K) to Tp = 343 K (Tm2x = 360 K) are represented. The kinetics of these motional modes obeys the ZEL as seen in the TSDC relaxation map (Fig. 2), which is a representation of the activation energy of the different modes of motion as a function of the temperature of the maximum intensity of the respective partial polarization peaks Fig. 1. TSDC motional modes of the secondary relaxations in brucine. (a) The lower temperature secondary motions (with smooth) corresponding to the y relaxation; the polarization temperatures were from 148 up to 203 K, every five degrees and the polarizing electric field strength was Ep = 300 V mm™ Fig. 2. TSDC relaxation map of brucine obtained from experiments carried out at 6 °C min-1: activation energy, Ea(Tm), of the partial polarization components of the different relaxations as a function of the peak's location, Tm. The dotted line is the zero entropy line and the arrow indicates the glass transition temperature provided by TSDC, TgTSDC = 368.5 K. The lower temperature points (orange diamonds in the online edition, in the proximity of the zero entropy line between 173 and 183 K) correspond to the local, fast y secondary relaxations, while the points in the vicinity of TgTSDC (blue triangles in the online edition, displaying a strong and continuous deviation from that line) refer to the cooperative modes of the «-relaxation of the orientational glass. The green circles, at temperatures close to Ts, correspond to the slow BJG secondary relaxation shown in Fig. 1(b). | |
train_160 | What is described in this image? | Microscale combustion calorimetry (MCC), which is a quantitative and rapid method, was used for comparison of the flammability of the cured DGEM/DDS and DGEBA/DDS. As illustrated in Fig. 9, the DGEM/ DDS showed lower peak heat release rate (PHRR) and total heat release (THR) than that of DGEBA/DDS, which were reduced up to 70% and 26%, respectively. This reduction indicated that the DGEM/DDS released much fewer combustible substances during the process of pyrolysis, which suggested that it exhibited lower flammability than DGEBA/DDS. The obtained PHRR, THR and time-to-ignition (TTI) (summarized in Table $3) were used to calculate the Flame Retardancy Index (FRI), which is a universal dimensionless criterion for evaluation of the flame retardancy of resin systems [62,63]. The FRI was calculated according to Eq. (1). Fig. 9. Heat release rate versus temperature curves form MCC tests for cured DGEM/DDS and DGEBA/DDS. | |
train_161 | What is described in this image? | Fig. 2 shows how well the new function fits the individual peaks of two different NiTi samples. Also a comparison with a standard Fraser- The asymmetry of the PW1 sample is less apparent. Both the onset and endset have comparable o values because the peak is more evenly distributed; however, the n and m values of the onset are larger than then endset because the endset has a more gradual transition. The peak for PW1 is broader than the peak for AW, which is reflected by much larger o values for PW1 than AW. The Fraser-Suzuki method does appear to match the PW1 curve well, however it still has a larger residual error than the newly proposed method. Overall, the new method does a much better job at curve fitting the data, as the standard methods do not have enough parameters to account for to non-standard shape of the NiTi transformation peaks. All of the relevant parameters for the new model are shown in Table 1. A comparison of the characteristic peak values is shown in Fig. 2. | |
train_162 | What is described in this image? | The thermal stability of these PEG samples was investigated using the TGA technique, and the measured curves are shown in Fig. 2. It can be seen from the results that the PEG samples behave a thermal decomposition starting in the temperature region from (523 to 623) K and ending at temperatures above 723 K. Also, the decomposition starting temperatures of the large molar mass PEG samples are higher than those of small molar mass samples. These thermal behaviour for PEG are similar with those reported by Karaman et al. [20]. Based on these results, it can be concluded that all the PEG samples are thermally stable in the heat capacity measurement region below 400 K. | |
train_163 | What is described in this image? | Figure 4 shows the first cycles of DSC- Figure 4. First DSC and dilatometry cycles (right) of Ti-14Nb in relation to the Ti–Nb phase diagrams (left). Dotted lines belong to the equilibrium &/B diagram. Gray areas represent the miscibility gaps in the metastable @/ B phase diagram. | |
train_164 | What is described in this image? | Fig. 8. Variation of the reduced isothermal cure rate, i., with the extent of cure, a, for EPO-1.0 at | |
train_165 | What is described in this image? | 3.4. Characterization of MMMs using differential scanning calorimetry The influence of the addition of MMTs on the glass transition temperature, T& of PEI/MMTs MMMs, is illustrated in Table 2, which shows that there are some changes in the To of the MMMs relative to the neat polymer. Since all of the temperatures were below the neat PEI Tg, it can be concluded that the structure is getting less crystalline and is moving toward the amorphous structure. 3.5. Field emission scanning electron microscope of mixed matrix membranes The morphology of MMMs strongly affects the MMMs performance [37]. Therefore FESEM was utilized to investigate the extent of the adhesion between filler particles and polymer matrix. The MMMs cross-sectional morphologies are illustrated in Fig. 5. We note that because of very low fillers concentration (1.0 wt.%), detecting the MMTs particles at the FESEM samples cross sections was very difficult. The FESEM micrographs shown are the outputs of a number of the MMMs samples. According to Fig. 5a, clear formation of void surrounding the raw MMT particles can be observed. Since no modification was carried out on the raw MMT, there was poor adhesion between the filler particles and the PEI polymer matrix. Fig. 5b illustrates excellent adhesion between the general MMT particles and the PEI polymer matrix. As a result of the adhesion, no void can be observed. This is speculated to be the result of a high degree of compatibility between the filler particles and the polymer matrix. The compatibility had been provided by industrial modification of the MMT particles via ammonium ion treatment. The same results are depicted in Fig. 5c for Cloisite 15A. A We note that because of very low fillers concentration (1.0 wt.%), detecting the MMTs particles at the FESEM samples cross sections was very difficult. The FESEM micrographs shown are the outputs of a number of the MMMs samples. According to Fig. 5a, clear formation of void surrounding the raw MMT particles can be observed. Since no modification was carried out on the raw MMT, there was poor adhesion between the filler particles and the PEI polymer matrix. Fig. 5b illustrates excellent adhesion between the general MMT particles and the PEI polymer matrix. As a result of the adhesion, no void can be observed. This is speculated to be the result of a high degree of compatibility between the filler particles and the polymer matrix. The compatibility had been provided by industrial modification of the MMT particles via ammonium ion treatment. The same results are depicted in Fig. 5c for Cloisite 15A. A We note that because of very low fillers concentration (1.0 wt.%), detecting the MMTs particles at the FESEM samples cross sections was very difficult. The FESEM micrographs shown are the outputs of a number of the MMMs samples. According to Fig. 5a, clear formation of void surrounding the raw MMT particles can be observed. Since no modification was carried out on the raw MMT, there was poor adhesion between the filler particles and the PEI polymer matrix. Fig. 5b illustrates excellent adhesion between the general MMT particles and the PEI polymer matrix. As a result of the adhesion, no void can be observed. This is speculated to be the result of a high degree of compatibility between the filler particles and the polymer matrix. The compatibility had been provided by industrial modification of the MMT particles via ammonium ion treatment. The same results are depicted in Fig. 5c for Cloisite 15A. A Fig. 5d and e show the morphology of hydrophilic MMT MMM and hydrophobic MMT MMM respectively. From Fig. 5d and e, void morphology, which was formed due to the poor inorganic-organic adhesion, is obvious. Hydrophobic and hydrophilic MMTs were prepared industrially by applying octadecylamine as the modifier, but our target of providing the desired adhesion between the two phases was not achieved. Fig. 5d and e show the morphology of hydrophilic MMT MMM and hydrophobic MMT MMM respectively. From Fig. 5d and e, void morphology, which was formed due to the poor inorganic-organic adhesion, is obvious. Hydrophobic and hydrophilic MMTs were prepared industrially by applying octadecylamine as the modifier, but our target of providing the desired adhesion between the two phases was not achieved. Fig. 9 depicts the influence of Cloisite 15A loading on the separation properties of MMMs. The amount of loading varies from 0.0 to 3.0 wt.% Cloisite 15A. Permeance exhibits an increasing trend in correspondence to the increase in MMT loading up to 1.0 wt.%, and then shows a descending trend. This phenomenon can be attributed to the Tg depletion which leads to an increase in matrix amorphous structure which in turn results in permeance enhancement. The decrease in permeance at the higher loading values can be interpreted due to high aspect ratio of MMT plates which play as berries across the gas diffusion path. Thus it can outweigh the effect of Tg depletion on MMM permeance. Among this interval of loading, the permeance of these MMMs is still higher than that of neat PEI. Fig. 9 shows the changes in selectivity as a function of Cloisite 15A loading. It is observed that at loadings of 0.5 wt.% and 1.0 wt.%, Cloisite 15A selectivity increases by 28% and 16%, respectively, relative to the neat PEI. Obviously this cases exhibit an ideal morphology (Fig. 5c). As mentioned previously, since MMTs have high aspect ratio dimensions, and moreover it was intercalated by tallow, the subsequent increase in selectivity can be explained in terms of an increase of tortuosity [38] and possibly the shape or size discrimination passing between the intercalated clay layers. Unlike these loadings, at higher loadings, the MMMs experience a dramatic decline in selectivity. The uniform dispersion of MMTs decreases as clay loading increases. At higher loadings, the filler | |
train_166 | What is described in this image? | Fig. 5. FTIR spectra of (a) pure Agar and Agar-RGO composite films with RGO concentrations of (b) 1 wt% and (c) 2 wt.% at various Temperatures. responsible during its transition, temperature-dependent FTIR spectra of Agar and its composites with different wt.% concentration of RGO have been recorded and are presented in Fig. 5. It is well clear from this figure that, increase in temperature from room temperature to 120 ℃ mainly influences the vibrational modes present in spectral region viz. | |
train_167 | What is described in this image? | 3.5. Dynamic mechanical thermal testing DMTA is a technique for applying stress to a material and measuring its response. Since polymers are viscoelastic by nature, the analysis will give information about the storage modulus and the loss modulus. As the storage modulus is conceptually equivalent to the modulus of traditional mechanical testing, it gives a measurement of the stiffness of the material. In this study, only the composites made from the hybrid yarns with a wrapping density of 250 were analysed. The results are shown Fig. 6. The storage modulus (at 20 °C) increased from 3.07 GPa for pure PLA up to 6.2 GPa for the composite with 45 mass% fibre (Fig. 6a). It is evident that incorporation of hemp fibres results in an increase in the storage modulus of the biocomposite which reveals effective stress transfer from the fibre to the matrix at the interface and good adhesion between the fibre and the matrix. These results are consistent with previously published results on natural fibre/ 3.5. Dynamic mechanical thermal testing DMTA is a technique for applying stress to a material and measuring its response. Since polymers are viscoelastic by nature, the analysis will give information about the storage modulus and the loss modulus. As the storage modulus is conceptually equivalent to the modulus of traditional mechanical testing, it gives a measurement of the stiffness of the material. In this study, only the composites made from the hybrid yarns with a wrapping density of 250 were analysed. The results are shown Fig. 6. The storage modulus (at 20 °C) increased from 3.07 GPa for pure PLA up to 6.2 GPa for the composite with 45 mass% fibre (Fig. 6a). It is evident that incorporation of hemp fibres results in an increase in the storage modulus of the biocomposite which reveals effective stress transfer from the fibre to the matrix at the interface and good adhesion between the fibre and the matrix. These results are consistent with previously published results on natural fibre/ The dampening, or tan 8, is the ratio between the loss modulus and the storage modulus and gives information about the internal friction of the material. For a composite, the molecular motion in the interface will contribute to the dampening. The dampening will consequently give information about the adhesion of the interface. There is a general trend of the data in Fig. 6b, with reduced tan ô values with higher fibre ratio. The same trend has also been observed by other authors for various reinforcements [37–39]. A possible explanation is that there is a strong interaction between the fibre and the matrix. For a composite with a low fibre ratio, the polymer chains are relatively free to move. Increasing the fibre | |
train_168 | What is described in this image? | Fig. 15. DSC scan of a very pure sample of sulphamerazine (3.6 mg). Heating rate, 2 deg min-1; program. dynamic purity V1.1. Found: purity, 99.81 mole%: ΔH. 45.8 kJ mole-1: For sulphamerazine, the DSC examination (Fig. 15) shows an endothermic reaction with a very sharp peak in the interesting temperature range. The reaction starts at 229.2°C and has peak temperature at 233.2°C. | |
train_169 | What is described in this image? | Good linear relations can be found between the Qoil and the corresponding wax contents determined by both standard acetone method and Qoil/Qwax method (see Fig. 2). Fig. 2. The relationship between wax content and the Qoll- | |
train_170 | What is described in this image? | Figure 7. Plot of Y [ , In(a/ T2); +, In(dx /dt) p; ▼, In(a/ Tp); A, Figure 6 shows the variation of In(a/Tp) with 1/ Tp. The slope of this approximated formula gives the value of activation energy for crystallization Ec given in table 2. Figure 7 shows the variation of In(dx/dt)p, In(a/T2), In(a), In(a) Tp-To) | |
train_171 | What is described in this image? | Fig. 8. Stress-strain curves for the neat and modified PLA (a) and PBAT (b) films. As a matter of fact, the modified PLA with Joncryl strain hardens more easily then the unmodified counterpart (Fig. 8) | |
train_172 | What is described in this image? | Furthermore, the results of dielectric constant and impedance plots have been confirmed by X-ray diffraction (XRD) study. Fig. 7(a-d) show the XRD patterns for CS:AgNt system and blend samples. Broad peaks were found in Fig. 7(a), which are ascribed to the amorphous nature of CS based electrolyte [23]. The peaks were furthermore broadened at 10 wt % PEO as depicted in Fig. 7(b). It is obvious from Fig. 7(c) that, at 30 wt % PEO, the intensity of the main peaks of PEO have been increased, which are originated from the ordering of side chains of PEO as well as the strong intermolecular interaction among PEO chains through the hydrogen bonding [18]. Other researchers have also observed these crystalline peaks for PEO based electrolytes at 20 ranges from 19° to 24° [18,21,27]. It is interesting to notice that, at 50 wt % of PEO, the intensity of crystalline peaks of PEO have been greatly enhanced, while the amorphous broad peaks were almost disappeared as shown in Fig. 7(d). Furthermore, the results of dielectric constant and impedance plots have been confirmed by X-ray diffraction (XRD) study. Fig. 7(a-d) show the XRD patterns for CS:AgNt system and blend samples. Broad peaks were found in Fig. 7(a), which are ascribed to the amorphous nature of CS based electrolyte [23]. The peaks were furthermore broadened at 10 wt % PEO as depicted in Fig. 7(b). It is obvious from Fig. 7(c) that, at 30 wt % PEO, the intensity of the main peaks of PEO have been increased, which are originated from the ordering of side chains of PEO as well as the strong intermolecular interaction among PEO chains through the hydrogen bonding [18]. Other researchers have also observed these crystalline peaks for PEO based electrolytes at 20 ranges from 19° to 24° [18,21,27]. It is interesting to notice that, at 50 wt % of PEO, the intensity of crystalline peaks of PEO have been greatly enhanced, while the amorphous broad peaks were almost disappeared as shown in Fig. 7(d). Furthermore, the results of dielectric constant and impedance plots have been confirmed by X-ray diffraction (XRD) study. Fig. 7(a-d) show the XRD patterns for CS:AgNt system and blend samples. Broad peaks were found in Fig. 7(a), which are ascribed to the amorphous nature of CS based electrolyte [23]. The peaks were furthermore broadened at 10 wt % PEO as depicted in Fig. 7(b). It is obvious from Fig. 7(c) that, at 30 wt % PEO, the intensity of the main peaks of PEO have been increased, which are originated from the ordering of side chains of PEO as well as the strong intermolecular interaction among PEO chains through the hydrogen bonding [18]. Other researchers have also observed these crystalline peaks for PEO based electrolytes at 20 ranges from 19° to 24° [18,21,27]. It is interesting to notice that, at 50 wt % of PEO, the intensity of crystalline peaks of PEO have been greatly enhanced, while the amorphous broad peaks were almost disappeared as shown in Fig. 7(d). Furthermore, the results of dielectric constant and impedance plots have been confirmed by X-ray diffraction (XRD) study. Fig. 7(a-d) show the XRD patterns for CS:AgNt system and blend samples. Broad peaks were found in Fig. 7(a), which are ascribed to the amorphous nature of CS based electrolyte [23]. The peaks were furthermore broadened at 10 wt % PEO as depicted in Fig. 7(b). It is obvious from Fig. 7(c) that, at 30 wt % PEO, the intensity of the main peaks of PEO have been increased, which are originated from the ordering of side chains of PEO as well as the strong intermolecular interaction among PEO chains through the hydrogen bonding [18]. Other researchers have also observed these crystalline peaks for PEO based electrolytes at 20 ranges from 19° to 24° [18,21,27]. It is interesting to notice that, at 50 wt % of PEO, the intensity of crystalline peaks of PEO have been greatly enhanced, while the amorphous broad peaks were almost disappeared as shown in Fig. 7(d). Furthermore, the results of dielectric constant and impedance plots have been confirmed by X-ray diffraction (XRD) study. Fig. 7(a-d) show the XRD patterns for CS:AgNt system and blend samples. Broad peaks were found in Fig. 7(a), which are ascribed to the amorphous nature of CS based electrolyte [23]. The peaks were furthermore broadened at 10 wt % PEO as depicted in Fig. 7(b). It is obvious from Fig. 7(c) that, at 30 wt % PEO, the intensity of the main peaks of PEO have been increased, which are originated from the ordering of side chains of PEO as well as the strong intermolecular interaction among PEO chains through the hydrogen bonding [18]. Other researchers have also observed these crystalline peaks for PEO based electrolytes at 20 ranges from 19° to 24° [18,21,27]. It is interesting to notice that, at 50 wt % of PEO, the intensity of crystalline peaks of PEO have been greatly enhanced, while the amorphous broad peaks were almost disappeared as shown in Fig. 7(d). | |
train_173 | What is described in this image? | Typical DSC behaviour of films from fish gelatin alone (G) or blended with lignin (G-L) are shown in Fig. 4. Films G exhibited thermal characteristics resembling those reported in a previous publication (Gómez-Estaca, Giménez, et al., 2009; Gómez-Estaca, Montero, et al., 2009) concerning a type A tuna-skin gelatin prepared at the laboratory. Essentially, the thermal behaviour of gelatin single films consisted (Trace G, solid line) of a glass transition process with a Tg ~ 18.5 ± 0.5 ℃, followed by an endothermic event involving a bimodal melting with maximum temperatures Tm at around 61.3 ± 0.5 °C and 79.5 ± 0.5 °C. These thermal data were something higher than corresponding ones of previous work, particularly Tg, which notwithstanding indicated a close similitude between that tuna-skin gelatin and current commercial warmwater fish gelatin. Melting enthalpy AH was 11.3 ± 0.41 J/gam- This kind of complex endothermic melting in G films has also been reported by Gómez-Estaca, Giménez, et al. (2009) and Gómez- Estaca, Montero, et al. (2009) and Rahmann, Al-Saidi, and Guizani Fig. 4. Normalized typical DSC traces (heat flow, W/gdm. vs temperature, °C) of films based on mixtures of fish gelatin (G) and lignin (L2000 and L2400) at the ratio 85% gelatin: 15% lignin (w/w). Single gelatin film, G; compound films with lignin, G—L1000 and G-L2400-First scans in conditioned films at -80 °C, solid lines; second scans, dash lines. First scans in conditioned films at 0 °C, dot lines. Arrows roughly indicate Tg locations: Inset shows DSC traces of blended films magnified in the temperature zone of the complex glass transition processes. Solid, first scans; dash, second scans. Bar indicates the ordinate scale (0.5 W/gdm) 54.9 ± 0.6 °C, respectively (Fig. 4). Tg data were significantly lower in G–L1000 than in G–L2400, this suggesting a differential plasticization capacity between both lignin types (L1000 > L2400). This glass transition process was followed by a second one at the significantly different Tg values of - 23.1 ±0.4 °C and - 20.6 ± 0.6 °C respectively. | |
train_174 | What is described in this image? | In Fig. 1, an example of IR spectra for T5651-based sample is shown. In order to study the influence of the hard Fig. 1. FT-IR-spectrum of PU film (5651/1/0/31; code is described in Table 1). Detail of the Fig. 1, i.e., wavenumber region from 1600 to 1800 cm-1 was used for further analysis; see Fig. 2. Fig. 1. FT-IR-spectrum of PU film (5651/1/0/31; code is described in Table 1). Detail of the Fig. 1, i.e., wavenumber region from 1600 to 1800 cm-1 was used for further analysis; see Fig. 2. | |
train_175 | What is described in this image? | The sequence of the interfacial reaction and the amount of elemental change can be gleaned from the EDS test data in Fig. 9. After 1 d of immersion, the small nuclei of HA or calcium phosphate can be detected on the surface of the powders. After 7 d, the powders are covered by HA and after 21 d the thickness of HA is so high that EDS could hardly detect the sodium and the silicon of the underlying powder. Fig. 9. EDS results of gel-derived and melt-cast 45S5 immersed in Simulated body fluid (SBF) for 0, 1, 14, and 21 d, (a) Ca plot, (t) Si plot, (t) | |
train_176 | What is described in this image? | Fig. 1. Total phenol content (a) and DPPH scavenging activities (b) of SSPS films with ZEO and MEO. Fig. 1 shows the total phenolic (TP) content of SSPS films incorporating ZEO and MEO. The TP content of pure SSPS used in this study was 11.3 mg GAE/100 g SSPS. TP content in the composite film significantly increased (P < 0.05) with increasing ZEO or MEO concentration (Fig. 1). The TP content was higher in the films with ZEO than those with MEO. Since the antioxidant capacity of food is determined by a mixture of different antioxidants with different action mechanisms, it is necessary to combine more than one method in order to determine in vitro, the antioxidant capacity of foodstuffs (Pérez-Jiménez et al., 2008). Therefore, the antioxidant activities of the composite SSPS films were investigated using the DPPH radical scavenging and ferric reducing power assay. A DPPH | |
train_177 | What is described in this image? | Figure 22. FTIR spectra for PLGA 70/30 (syntheses 1 and 3) and PLGA 50/50 (syntheses 2 and 4). | |
train_178 | What is described in this image? | ~747 cm-1 corresponds to Li-coordinated TFSI anions in the crystal lattice. In the electrolyte spectrum, on the other hand, the single peak at 740 cm-1 (Fig. 5) has a slight asymmetric broadening and there is a small peak at 761 cm-1 attributed to PMMA. For the main feature the fitting procedure reveals peaks at ~740cm=1 and Fig. 5. Raman spectrum of the PEGMA83 SPE in the 720-780 cm-1 region, showing the contributions of the "free" TFSI anions (740 cm"}) and the Li"-TFSI ion pairs | |
train_179 | What is described in this image? | after the starch sample was held at 10℃ below gelatinization onset temperature for 2 h (Fig. 5A). After further annealing the partially heated starch-water mixture at -7°C for 30 min, the glass transition temperature increased to -4.0℃ and became more evident (Fig. 5B). Gelatinization enthalpy was not changed after the starch solution Fig. 5. DSC thermograms of a native waxy corn starchwater system (1/2, w/w) after being (A) preheated to 10°C | |
train_180 | What is described in this image? | To gain more insight on the magnetic state, we performed zero-field as well as weak-transverse-field (WTF) uSR measurements up to 500 K. uSR measurements in the WTF configuration are used to determine the volume fractions of sample regions with and without static magnetic order. A persistent oscillation amplitude in WTF uSR spectra would reflect the fraction of the muons ensemble (i.e., fraction of the sample volume) with a nonmagnetic environment. Figure 3 shows the precessing amplitude of the obtained WTF uSR signal normalized to its value obtained in the paramagnetic state. Up to about 475 K, the uSR amplitude is very low, indicating that CS0.8 (FeSe0.98)2 is still in a magnetic state. Upon increasing the sample temperature above 479 K, a steplike increase of the WTF uSR amplitude is observed indicating the transition to a paramagnetic state at higher temperature [15]. The fact that the whole sample orders at a well defined ordering temperature again proves the homogeneity of our sample and excludes possible impurity phases to be (ATN is the width of transition) to the data (solid line in Fig. 3) [16]. The sharpness of the transition [ATN = | |
train_181 | What is described in this image? | 3D-printed sample reported in Figure 8. In addition, the strain rate reached by PLA/HA composites is comparable to that of the conventional plastics used in FDM, that is, about 1 mm/ | |
train_182 | What is described in this image? | Fig. 2 Packing diagram of 1 in the HTP along (a) the a direction and (b) | |
train_183 | What is described in this image? | Fig. 1. One formal molecule of investigated crystal. | |
train_184 | What is described in this image? | DSC Studies. Thermoreversible study was further confirmed by DSC analysis. Figure 8 shows the heating and cooling curves of DSC analysis of the FEF-2- BM and DA cross-linked polymer. Figure 8a shows the first heating curve of the cross-linked polymer heated at -100 to 200 ℃. The curve "A" shows the first heating cycle. It has an endothermic peak at 150 ℃, which indicated the cleavage of the DA cross-links. The curve "B" shows the cooling curve of the polymer. It shows a broad exothermic peak at 122-180 ℃ due to the covalent bond formation between furan and maleimide moieties, as the samples come closer on cooling and then finally reconnect very efficiently. The curve "C" shows the second heating cycle of the DA cross-linked polymer. It also shows the same observation in the first heating cycle. It clearly indicates that the Diels-Alder crosslinked block polymer (FEF-2-BM) is thermoreversible. The T s of the polymer were determined from the second heating cycle of the polymers and are shown in Figure 8b. The transition at 114 ℃ is due to the Tg of the hard segment (PFMA-BM). The shifting of hard segment T2 from +65 to 114 ℃ is due to the DA cross-linked between PFMA and BM. The transition at -44 ℃ (Figure 8b) is due to the Tg of Figure 8. DSC analysis of the polymer. (a) DSC curve for the cross-linked polymer poly(furfury) methacrylate)-poly(2-ethylhexyl acrylate)- b-poly(furfuryl methacrylate)-2-bismaleimide (FEF-2-BM):( A) first heating curve, (B) cooling curve, and (C) second heating curve. (b) T , of the crosslinked polymer. | |
train_185 | What is described in this image? | * Determined from phase diagrams in Fig. 1a-j. The results from the Schrader equation are plotted in the form of the phase diagrams for the binary and pseudo-binary eutectic PCMs in order to determine the eutectic mass ratios and the eutectic point as shown in Fig. 1a-j. It is evident from the phase diagrams of the binary eutectic mixtures LA/PT68, MA/PT68, PA/PT68, SA/PT68 and SA/PA as shown in Fig. 1a-e, that the onset melting temperature of the individual components (LA, MA, PA, SA, and PT68) is greater than the identified eutectic point of the respective binary eutectic PCM. The onset melting temperature of the individual PCMs employed in this study as provided by the supplier are presented in Table 1. Onset melting temperature of the components involved in the ternary (SA-PA/ The results from the Schrader equation are plotted in the form of the phase diagrams for the binary and pseudo-binary eutectic PCMs in order to determine the eutectic mass ratios and the eutectic point as shown in Fig. 1a-j. It is evident from the phase diagrams of the binary eutectic mixtures LA/PT68, MA/PT68, PA/PT68, SA/PT68 and SA/PA as shown in Fig. 1a-e, that the onset melting temperature of the individual components (LA, MA, PA, SA, and PT68) is greater than the identified eutectic point of the respective binary eutectic PCM. The onset melting temperature of the individual PCMs employed in this study as provided by the supplier are presented in Table 1. Onset melting temperature of the components involved in the ternary (SA-PA/ and quinary (SA-PA-LA-MA/PT68) eutectic PCMs are also greater than the eutectic point determined from phase diagrams of these pseudobinary eutectic mixtures as shown in Fig. 1f-j. Calculated eutectic mass composition, eutectic point, specific heat capacity and the latent heat of fusion of the eutectic PCMs are consolidated in Table 2. The percentage mass composition and the eutectic point (onset melting temperature) of these binary and pseudo-binary eutectic PCMs are identified from their respective phase diagrams. The specific heat capacity for both the liquid and solid phase of respective eutectic PCMs is estimated using Eq. (3), | |
train_186 | What is described in this image? | Figure 7 SEM photographs of the impact fracture surface of PLA/MBS blends: (a) 100/0, (b) 95/5, (c) 93/7, (d) 90/10, As could be seen from Figure 7(a-c), the fracture surface of 100/0, 95/5, and 93/7 PLA/MBS blends showed relatively smooth, indicating that little plastic deformation had taken place during the impact test. This was in good agreement with their lower impact strength. From Figure 7(d-f), the fracture surface of 90/10, 85/15, and 80/20 PLA/MBS blends were rough and had many root-like whiskers and many long stretches of the ligaments, which As could be seen from Figure 7(a-c), the fracture surface of 100/0, 95/5, and 93/7 PLA/MBS blends showed relatively smooth, indicating that little plastic deformation had taken place during the impact test. This was in good agreement with their lower impact strength. From Figure 7(d-f), the fracture surface of 90/10, 85/15, and 80/20 PLA/MBS blends were rough and had many root-like whiskers and many long stretches of the ligaments, which Such fibril-like structures have been reported in other rubber modified polymers.34-37 For the 85/15, 80/20, and 75/25 PLA/MBS blends, the impact caused not only the fibrils but also some cavitations and a clear matrix deformation. In Figure 7(d-g), cavitation can be clearly identified. The large voids might be formed by the coalescence of neighboring small cavities. Figure 7(g) displayed the ductile fracture on which rumpled surface could be seen. The rumples lied parallel to the notch and gave rise to tufts of highly drawn material. Such fibril-like structures have been reported in other rubber modified polymers.34-37 For the 85/15, 80/20, and 75/25 PLA/MBS blends, the impact caused not only the fibrils but also some cavitations and a clear matrix deformation. In Figure 7(d-g), cavitation can be clearly identified. The large voids might be formed by the coalescence of neighboring small cavities. Figure 7(g) displayed the ductile fracture on which rumpled surface could be seen. The rumples lied parallel to the notch and gave rise to tufts of highly drawn material. | |
train_187 | What is described in this image? | 3.1. Characterization of the form-stable composite PCMs Fig. 2 shows the photos and SEM images of expanded VMT before and after CA-LA impregnation. As seen in Fig. 2(a) and (b), 3.1. Characterization of the form-stable composite PCMs Fig. 2 shows the photos and SEM images of expanded VMT before and after CA-LA impregnation. As seen in Fig. 2(a) and (b), photograph views of expanded VMT are very similar before and after PCM impregnation. However, the microstructure of expanded VMT had changed as seen in Fig. 2c and d. That is, the pores of expanded VMT were completely filled with CA-LA eutectic mixture after the impregnation process. Similar photograph views and SEM images were also observed for the form-stable CA-PA/VMT and CA- SA/VMT composite samples. The SEM images also show that the expanded VMT has an excellent absorbability with strong capillary force and surface tension with multiple pores and organic compounds such as fatty acids can be absorbed easily in its pores. Fig. 2. The photograph views and SEM images of expanded VMT before and after CA–LA impregnation. | |
train_188 | What is described in this image? | Fig. 3. Normalized average tensile strength with standard deviation of GFRP bar specimens tested under different temperatures | |
train_189 | What is described in this image? | (80 ml min) from 300 K up to 500 K at a constant heating rate of 2 K min-1. The temperature was measured by a Pt-Pt/Rh thermocouple with the accuracy of ±0.5 K. Fig. 2 presents a comparison of the TG, DTG and DTA curves for HCC in the temperature range of 300-380 K. It can be seen from TG Fig. 2. TG, DTG and SDTA curves for HCC at 300-380 K. | |
train_190 | What is described in this image? | To further confirm the structure of PSA, 1H NMR measurements were employed to characterize the product. Fig. 2 shows the 1H NMR spectra of PEPA, intermediate and PSA. A strong resonance signal at around 4.58 ppm in the spectra of PEPA, intermediate and PSA is similarly characteristic of the protons (labeled a) of methylene in the spiro structure. As for the spectra of intermediate, it can | |
train_191 | What is described in this image? | To explain these differences, attention must be paid to the filament deposition process in which the molten polymer is extruded from the nozzle and deposed on the already printed part (Figure 10). Moreover, to a lesser extent, filament stretching occurs also in the semimolten state due to the speed gradient between the filament speed and printing speed (Figure 10). For PLA 4032D, at increasing printing temperature, the polymer matrix is more relaxed avoiding chain orientation and stretching phenomena. On the contrary, in the case of PLA 4032D+C30B, the presence of clay platelets reduces PLA relaxation at the same time allowing the orientation both of layered silicates and the polymer matrix. Thus, as widely known, higher mechanical properties are obtained when polymer and clay orientation occur [7,8]. Figure 10. Schematic representation of the filament deposition process and detail of the nozzle. | |
train_192 | What is described in this image? | The degradation of both BSPUs samples was also evident by FTIR (Fig. 3). PCL hydrolysis was observed in the carbonyl region as this absorption shifted from 1728 cm-1 to 1712-1706 cm-1, which corresponds to hydrogen bonded C=O in the urethane. After alkaline or acidic hydrolysis, the BSPU1 carbonyl peak broadened while OH absorption at 3550 cm-1 increased (Fig. 3a), suggesting that PCL has also been partially hydrolysed to render carboxylic and hydroxyl groups. In the case of BSPU2, alkaline hydrolysis led to a significant reduction in the carbonyl peak, suggesting a degradation of the rigid segments too. This was corroborated after the degradation of the model HMDI–DTE polyurethane, which lost 58% of its mass in 5 M NaOH. The degradation of both BSPUs samples was also evident by FTIR (Fig. 3). PCL hydrolysis was observed in the carbonyl region as this absorption shifted from 1728 cm-1 to 1712-1706 cm-1, which corresponds to hydrogen bonded C=O in the urethane. After alkaline or acidic hydrolysis, the BSPU1 carbonyl peak broadened while OH absorption at 3550 cm-1 increased (Fig. 3a), suggesting that PCL has also been partially hydrolysed to render carboxylic and hydroxyl groups. In the case of BSPU2, alkaline hydrolysis led to a significant reduction in the carbonyl peak, suggesting a degradation of the rigid segments too. This was corroborated after the degradation of the model HMDI–DTE polyurethane, which lost 58% of its mass in 5 M NaOH. Fig. 3a and b also shows that oxidative degradation did not affect the carbonyl absorption at 1728 cm-1, indicative of the presence of both ester and urethane linkages. Separate experiments conducted to assess PCL oxidation in H₂O₂ did not show a significantly different FTIR spectrum (data not shown) as only a reduction in the 1295 cm=1 band, associated with its crystalline phase, was observed. The urea band located at 1632 cm ¯¹ also diminished, suggesting that the urea linkages are susceptible to oxidation. Degraded Tecoflex® in different media did not show a significant change in their FTIR spectra (Fig. 3c) and only small changes in the 3330 and 1660 cm-1 absorptions were observed during the oxidative degradation. Fig. 3a and b shows the infrared spectra for BSPU1 and BSPU2. | |
train_193 | What is described in this image? | The specific volume of the amorphous phase Vg against Figure 6. Figure 6 shows the calculated specific amorphous volume Va which can be fitted by an exponential function with the parameters A = 1.168 (±0.006), B = - 0.083 (±0.006), and C=17.2 (±3). Va increases with increasing branching until saturation is reached at higher content of a-olefin comonomer. The saturation level may differ for different types of comonomers. Because of the statistical scatter of data we ignore here, however, this effect. | |
train_194 | What is described in this image? | DSC analysis of Sn1_>Pb2Se reveal that the T decreases almost linearly at a rate of ~ - 3.2 K per x with increasing x up to ~0.2, the solubility limit of Pb (Figure 4). For example, Figure 4. Differential scanning calorimetry analysis of Sn __ Pb,Se (x = TS) that determines the phase transition phenomenon. PbSe alloying can be regarded as forming the defect in SnSe crystal structure and would be endothermic because the resulting lattice disruption raises the enthalpy (H) of Sn1_>Pb2Se (Figure 4). At the same time, the induced disorder also contributes to elevating its entropy (S). The -TS term becomes more negative with higher PbSe content or temperature. Upon heating, the minimum in the Gibbs energy shifts to lower temperature with the higher PbSe alloying fraction. Correspondingly, the T of Sn1_>Pb,Se could diminish with increasing x. This finding is substantially important in SnSe thermoelectrics exhibiting the considerable decrease in bandgap | |
train_195 | What is described in this image? | whose dimensions change drastically (~100% increase in length and 50% reduction in thickness) under mechanical stimulation (Figure 1 and Movie S1), similar to the malleable deformation of metals. However, it was confirmed by the single-crystal X-ray diffraction (SCXRD) studies that the visible deformation process is a strict oriented SCSC phase transition, which enables us to obtain concrete information about the changes in crystal packing on the same sample after the phase transition. Thus, this particular SCSC phase transition provides a good model to understand the structure-property relationships between crystal dimension changes and crystal structures. Figure 1. SCSC phase transition process with the (001) plane of Form II as pressure-bearing surface. | |
train_196 | What is described in this image? | The effect of heating rate on the transition in wool aged 52 days at 20℃ is shown in Figure 2. The transition decreases in size and temperature as the heating rate decreases. Similar effects were obtained for polystyrene, and the effect of heating rate on both materials is summarized in Figure 3. The values shown here were corrected for the shift in the indicated temperature with scanning rate. This correction was obtained from melting point determinations on azobenzene (Tm 63.1°C; 10 dpm) with heating rates of 2 to 50 dpm. For amorphous polymers, the glass transition occurs when extensive cooperative segmental motion of polymer chains occurs. Calorimetric measurements do not show the effect of segmental motion directly but indicate changes in the molecular environment. The shift in the transition phenomena with heating rate is associated with the ability of the polymer to respond to the temperature change. The data in Figure 3 show wool are more dependent on the heating rate than polystyrene, and this may reflect the differing chemical structure of the hydrogenbonded wool water matrix and the amorphous polystyrene. | |
train_197 | What is described in this image? | Contour plots for E' and Tan (8) are shown in Fig. 18a-b. Using these contour plots, desired E' and Tan (8) corresponds to a particular annealing time, and temperature can be obtained for application requirements. Fig. 17 Normal probability plots for a) storage modulus and b) damping factor Fig. 18 Contour plots for a) | |
train_198 | What is described in this image? | The glass transition temperatures (Tg) of BR9000, HTPB and EHTPB were determined by DSC within the temperature range from -150 °C to 50 °C under nitrogen atmosphere (Fig. 11). The T2 of polydienes was greatly influenced by their chain microstructure and butadiene rubber (BR9000) with high cis-1,4 content possessed a very low Tg at -106.1 °C due to its flexible long cis-1,4 polybutadiene chains. When the C=C double bond in BR9000 were partly broke down and hydroxyl groups were introduced into the cis-1,4 polybutadiene chain ends simultaneously, the To slightly increased to -104.6 °C (HTPB). In comparison with HTPB and EHTPB, the existence of epoxy groups along the polymer chains in EHTPB made its microstructure more irregular than HTPB and led to a further increased To of EHTPB. And the higher epoxy percent of EHTPB resulted in a higher To of EHTPB. For example, when the epoxy percent increased from 6.7% to 14.0%, the To of EHTPB increased from -98.6 °C to -91.4 °C (Fig. 11). The disappearance of melting peak in EHTPBs indicated that the crystallization domain was weakened owing to their irregular microstructure. However, even if the introduction of the epoxy groups into the polymer chain disturbed the microstructure of cis-1,4 polybutadiene, the glass Fig. 11. DSC curves of BR9000, HTPB4, EHTPB10–4.8, and EHTPB17–4.8 (2nd heating curves). | |
train_199 | What is described in this image? | Fig. 8. Temperature of maximum intensity of the partial polarisation peaks, Tm. as a function of the corresponding polarisation temperature, Tp. The points on the lefthand side, with To between –140 and –110°C, correspond to the ß-relaxation of salicin (peaks in Fig. 5). The points with To between 8 and 30°C correspond to the sub-T& relaxation at ~25°C (some of the corresponding peaks are shown in Fig. 7). a single relaxation time, i.e. a non-distributed relaxation. It is to be noted that this behaviour is markedly different from that observed for the secondary relaxations (points in the left-hand side of Fig. 8). |
Subsets and Splits
No community queries yet
The top public SQL queries from the community will appear here once available.