The potential of hydrostatic weighing of partially crystalline polymers in an inert liquid during the study of their amorphization and crystallization processes over a broad temperature range was demonstrated using the low-density polyethylene-polymethylsiloxane system as an example.Professor Kirill Evgen'evich Perepelkin was, at a minimum, an extraordinary being among domestic (Soviet and Russian) polymer scientists studying problems of chemical fiber technology. The scope of his scientific interests was exceptionally broad. However, the relationships of the properties of natural and synthetic polymers to their structure and the formation conditions of the latter practically constantly interested him. Therefore, the two articles on this theme that are published below by representatives of the Ivanovo school of polymer chemists, some of whom had the pleasure of conversing personally with Kirill Evgen'evich, have become by a twist of fate a symbol of our parting with this remarkable person and scientist.Hydrostatic weighing [1, 2] is a method aimed at studying structure transformations in partially crystalline polymers that are due to the temperature and thermodynamically active liquids under the condition that the polymer remains in the solid phase during the course of the experiment and does not contain fractions that are soluble in the given liquid in the studied temperature range. The practical capabilities of the method were published earlier [1-3].Obviously replacing a liquid that is thermodynamically active relative to the polymer by a thermodynamically inactive one will automatically fulfill the insolubility condition regarding fractions of any molecular weight. Therefore, it becomes possible to measure the weight in the liquid of a polymer that exists also in the liquid phase, i.e., the melt.Such an experiment is interesting from two viewpoints. First, the true temperature of full amorphization (melting of the last crystals) of a partially crystalline polymer can be determined as the intersection of the temperature dependences of the solid and liquid (melt) polymers. Second, the nature and extent of structural transformations of the polymer matrix related to the change of its molecular packing density can be judged from the time dependences of the polymer density at a constant temperature.Herein the amorphization of low-density polyethylene (LDPE) in polymethylsiloxane PMS-20 medium is examined as an example of the practical implementation of these capabilities.The subject of the study was LDPE (15083-020 grade, GOST 16377-77) with melt index 1.32 ± 0.2 g/10 min (IIRT-5M instrument, 190°C, load mass 2.16 kg) as disks (20.0 ± 0.2 mm diameter, 3.0 ± 0.1 mm thickness) prepared by pressing granules at 160°C followed by cooling in air.

Hydrostatic weighing of a polymer in an immersion liquid using low-density polyethylene as an example was used to show that a condition for the lack of recrystallization of partially crystalline polymers upon annealing is the attainment at this temperature of thermomechanical equilibrium that determines the ratio of the amounts of macromolecule elementary units existing in amorphous and crystalline regions during the crystallization of these polymers. A basis was found for the viewpoint that the Gibbs-Thomson equation is applicable only for estimating the dimensions of the last (not bonded to each other by connecting chains) crystallites disappearing at the true melting point.It is commonly thought in discussing crystallization processes of polymers with flexible chains from the melt, their additional crystallization (melting-recrystallization) during annealing, and complete melting [1-8] that these polymers are biphasic (crystalline and amorphous phases) and thermodynamically non-equilibrated (metastable).The experimentally observed manifestations of the metastability of partially crystalline polymers are: -a lower melting point (mp) than the equilibrium value ( 0 m T ) characteristic of ideal crystals; -a dependence of the mp on the heating rate and the thermal history of the sample; -additional spontaneous crystallization with a decrease of the glassification temperature of amorphous regions to the ambient temperature.Additional crystallization was clearly evident during successive stepwise heating of a partially crystalline polymer undergoing hydrostatic weighing in an immersion liquid. Additional crystallization of low-density polyethylene (LDPE) pressed at 160°C and crystallized in air at room temperature (mp = 111.2 ± 0.4°C) was distinctly observed in the range 58.5-110.2°C with such a heating regime [9]. Apparently only amorphization occurred in the range 29.3-58.5°C. Anyway, preliminary storage of the sample in a differential scanning calorimeter cell for 1 h at 40°C was accompanied by a decrease of its heat of fusion (ΔH m ) by 6% [glassification temperature (T g ) of this LDPE sample was about -53°C].Strictly speaking, these results were expected and agreed completely with existing concepts about the thermal behavior of partially crystalline polymers. However, the problem is that if the postulates of Gibbs regarding phase equilibria are strictly adhered to [10], then such polymers should be viewed as monophasic microheterogeneous metastable liquids in which the ratio between the amount of macromolecule elementary units located in the amorphous regions and crystallites is determined by the thermomechanical equilibrium conditions [11].Such treatment of the monophasic state of partially crystalline polymers differs in principle from that proposed earlier [3, p. 326] in that the amorphization process of such polymer liquids is considered to be a first-order phase transition complicated by a three-dimensional strain deformation relative to regions with long-range three-dimensional ordering in the space aro...

Ключевые слова: социально-экономические показатели, потребительский спрос, корреляционнорегрессионный анализ, структурные уравнения, кластерный анализ Аннотация Предмет. Зависимости между региональными социально-экономическими показателями и объемом различных видов кредитов для физических лиц, совокупный портфель которых выступает одной из институциональных детерминант потребительского спроса. Рассмотрение широкого набора характеристик для поиска оптимальных форм взаимодействия и согласования интересов государства, реального и банковского секторов и общества в социальноэкономических преобразованиях, направленных на удовлетворение потребностей и повышение благосостояния населения, является новой постановкой вопроса для анализа. Цели. Дифференциация регионов в разрезе аспектов, влияющих на кредитование физических лиц. Методология. Исследование разделено на два этапа: проверка социальноэкономических показателей, а именно: исследована зависимость объема выданных кредитов для физических лиц и, дополнительно, ипотечных и жилищных кредитов от ряда показателей на основе корреляционно-регрессионного анализа и с помощью системы линейных структурных уравнений; по анализируемым социальноэкономическим показателям методами кластерного анализа осуществлено дифференцирование регионов. Результаты. Выявлено, что при построении классификаций по различным показателям и с помощью разных методов может наблюдаться определенное соответствие и даже близость полученных инструментальных результатов. Однако детальный анализ объектов в одной совокупности (кластере) выявляет существенные расхождения как по одному, так и по нескольким факторам и требует отнесения их к разным группам. Содержательная интерпретация сходства и отличий регионов позволяет скорректировать результат, учесть специфику каждого субъекта и сформировать предпосылки для принятия взвешенных решений в управлении многочисленными территориями. Выводы. Исследование может быть использовано в качестве содержательной и инструментальной основы для дальнейшей разработки рекомендаций федеральной и региональной власти при решении задач формирования потребительского спроса и оценки его влияния на развитие экономических систем различного уровня.

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The studies conducted led to the following conclusion: Brief, for no more than 2 min, activation of cellulose by dry grinding produces solutions of cellulose in MMO-DMSO mixture that have elevated homogeneity and require insignificant preparation time; this will probably favor their technological processing into fibres and films.The solvation characteristics, structure, and properties of nonaqueous solutions of cellulose and its derivatives have been insufficiently investigated. As a result, it has not been possible to deliberately regulate the characteristics of the medium and select the optimum versions of dissolution of cellulose and its processing into fibres, films, and other materials with unique physicomechanical properties in production [1, 2].We investigated the activating effect of mecbamcal treatment on the supermolecular structure and reactivity of cellulose. Samples of'Baikal sulfite cellulose with a degree of polymerization (DP) of 670 were investigated. A mixture of methylmorpholine N-oxide (MMO) monohydrate and dimethylsulfoxide (DMSO) in the ratio of 6:4 was used as the solvent.The solutions of cellulose in the mixed solvent were prepared in a thermostated cell with intense stirring; the temperature of dissolution was 363 K.To increase the solubility of the starting cellulose and facilitate its processing into fibres and films, the polymer was activated by dry grinding in a laboratory apparatus with an abrasive-impact action. The duration of the treatment was 0.5, 1, 2, and3 rain.The DP of the starting and modified cellulose was determined by the viscometric method in a mixture of trifluoroacetic acid and 1,2-dichloroetbane in the ratio of 7:3 with a method that we developed [3]. The degree ofcrystaUinity of the polymer was calculated with the data from x-ray structural analysis (DRON-3 diffractometer) using CuKo~ radiation, and the specific surface area of the polymer was determined by sorption of Congo red direct dye [4].The heterogeneity parameters were determined with the turbidity specmma. The degree of turbidity was measured on an SF-10 spectrophotometer in the 420-580 nm region of wavelengths X with a step of 20 nm.The degree of turbidity r t was calculated with the equation [5]where D x is the optical density at wavelength X; l is the cuvette length, cm. The double logarithmic graph of log ~'t -log h was then plotted and used to find the value of the wave exponent n (r t = X -n) as the tangent of the slope of the line. The scattering constant K and relative particle size ix, tabulated with respect to n and m, where m is the relative refractive index equal to the ratio of the refractive indexes of the polymer and dispersion medium, were determined from a table of characteristic functions [6] aXo r = N = 2n~o ' .[ t gT[ r-where ~ is the average wavelength in the range of the measurements; #o is the refractive index of the disperse medium.