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5Journal of Siberian Federal University. Engineering & Technologies 1 (2014 7) 3-12
УДК 504.5: 620.193.16
Hydrodynamic Dispersion
of Calcium Aluminosilicate from Technogenic
and Nonmetallic Materials
Liudmila V. Kashkinaa, Olesya P. Stebelevaa*, Tatiana Y. Emelyanovaa, Eleonora A. Petrakovskayab and Oleg A. Bayukovb
aSiberian Federal University, 79 Svobodny, Krasnoyarsk, 660041, Russia bL. V. Kirensky Institute of Physics SB RAS 50/38 Akademgorodok, Krasnoyarsk, 660036, Russia
Received 05.12.2013, received in revised form 18.12.2013, accepted 24.01.2014
Physicochemical properties of two calcium aluminosilicate materials after reducing in the hydrodynamic rotary generator in supercavitation mode were studied. The samples are the crystal ceramic foam based on Kansko-Achinsk lignite-ash and the porous glass material obtained from low-manganese nonmetallic feed. X-ray phase analysis, EPR-method, NPR-method (the Mossbauer Effect) and optical microscopy were used. It was found that the material is changing its stucrure in a hydrodynamic dispersion process caused by high-cavitation. The nature of the changes depends on its initial state.
Keywords: hydrodynamic dispersion, cavitation, crystal ceramic foam, porous glass material.
Introduction
Currently, treatment processes of technogenic materials allowing not only to extract the most valuable components of the waste, but also to obtain new materials with desired properties are developed and implemented. However, these technologies are energy intensive, since more than 50 % of the energy consumed for cominution of the basic substance. Recent studies have shown that energetically low-cost technology of hydrodynamic dispersion (crushing in a liquid medium) can be successfully used for fine powdering [1-8]. In [8] it was shown that used rotary hydrodynamic generator of low productivity under specified modes for 1 minute of dispersion at the initial average ash size of 175 microns produces an particle with average size of 25 microns, i.e. ash particles are "grind down" by almost 7 times ( the concentrations less than 3 wt %). If dispersed ash with an average initial size of 25 microns under the same conditions, then the output can be obtained particles having an average particle size of 3,5 - 4 mkm. Thus, in two phases (2 min. dispersion) particle size can be reduced from 175 microns to 4 microns, i.e. by more than 40 times. At higher
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* Corresponding author E-mail address: [email protected]
a feM
o.oo -,-
1M 1» MB
Particle sue . micran
Fig. 1. The density function of particle size distribution: 1 - initial ash, 2 - ash after dispersion (concentration 3 %), 3 - ash after dispersion "with increased (25 %) concentration
concentrations (25 %) dispersion effect is considerably less. Ash can grind from 175 microns to (50 mkm (Fig. 1).
One of thema(n factors determining the efficiency of the technology is the cavitation effect (from Lat. Cavitas - emptiness), which occurs due to sudden sharp pressure reducing in 5he flow of a moving fluid (hydrodynamic cavitation). Cavitios filled with gas, vapor or a mixture thereof (cavitaiion bubbles, taviiies) are iormed in a liquid. As a resule, she concenSration oi mechanical energa of the fluid in verw small volumes of cavitation bubbles, a high density of energy, according to some estimates up to l015 J/m3 [9]. Crushing occurs at high energy exposing of cumulative fluid microjets and shock waves generated by the collapse of cavitation bubbles on the solid particles. The temperature and pressure near the collapsing bubbles can be above 2000 K and 100 MPa [9, 10].
Experimental technicues
Phyrical basis of cnvitational effects are studied well, but the consequences to which they leai, are not always known. In view of the complexity of higgjii-eneirggy caviSation peocesses is the dispersion, theoretica) and experimental nescarca ih fhis area it relevant for the; development of efficient treatment processes for technogenic materials. A study was made of hydrodynamic dispersion of materials from industrial waste produced by the method of pyrometallurgical melting in a reducing medium [11]. Two kinds of calcium aluminosilicate powder of average dispersion (100 to 200 microns) were investigated:
1. The crystalline material was - ceramic foam. Ii is produced It}1 a self-propagaSing crystallization during remelting of silica foam from Kansko-Achinsk lignite-ash. Ash composition (wt %): SiO2 -45-54; CaO - 15-33; Al2O3 - 5-12; C - 1-2; Fe[x]O[y] - 7-11; MgO - 3-6; Na2O - 0,1-1; SO3 - 0,1-0,6; TiO2 - 0,1-0,3; K2O - 0,8-1,5; it also contains impurities of transition metals such as Ti, Mn, Cr, etc. The ceramic foam consist of anorthite crystal structure, gehlenite, wollastonite, iron oxides, transition metals Ti, Mn, Cr, etc. in small quantities.
2. The porous glass material derived from the melt of nonmetallic materials low in of manganese by the thermal shock method. The composition is (wt %): S1O2 - 44,41; CaO - 32,46; M2O3 - 7,82; Fe2O3 - 1,14; MnO - 4,88; MgO - 0,71; Na2O - 0,16; SO3 - 0,1-0,6; TiO2 - 0,186; K2O - 1,82.
The dispersion was carried out in the hydrodynamic rotary generator with two-bladed wedge impeller in mode supercavitation. Engine power - 1 kW, volume of the working chamber - 3^10-4 m3. At supercavitation mode, the bubbles are located in the tail of nonstationary supercavities, generated behind the rotor and the stable cavitation effect on the dispersing phase without destroying the impeller is implemented [10]. Three-percent water suspension of the glass and the ceramic foam powders is processed for 2 minutes at the rotor speed 10 000 r/min.
That said the part of the dispersed phase precipitated, and another part remained in a state of stable suspension. The precipitate and the suspension was dried in a Petri dish at temperature of 250 °C for 72 hours. The study was carried out by method of optical microscopy, XRD (diffractometer SMART APEX II), NGR - Mossbauer Effect (MS1104Em spectrometer), EMR (X-band spectrometer SE/X-2544).
Intrpritation and discussion of research results
According to the data of optical microscopy particle size of the ceramic foam and glass ceramics decreased by an average almost an order - to a fineness state after dispersion [12]. XRD spectra of the initial sample ceramic foam (diffractometer SMART APEX II), are characteristic of crystalline material (Fig. 2). The spectra are well manifested phase lines of anorthite CaAl2SO8 (d = 3,20; 2,95; 2,14 A), gehlenite 2CaO SiO2 Al2O3 (d = 2,30; 2,04 A), wollastonite Ca SiO3 (d = 2, 97; 2,80; 1,83 A), hematite Fe2O3 (d = 2,69; 2,53; 2,20 A).
We obtained sediment and suspension after the dispersion of the sample. The XRF spectrum profile of sediment is similar to spectrum of the initial sample, but changes were also observed. Along with the decrease in intensity of some lines until their disappearance there are new well resolved lines of such phases as Al (OH)3 (d = 4,34; 2,23; 2,03; 1,67 A), Al2O3 * H2O (d = 3,99; 3,214; 2,558 A), Al2 (OH)4Si2 (d = 7,17; 3,847; 3,37 A), which wasn't in the initial sample. In other words both partial destruction of the crystal structures of the material and synthesis of new compounds with the active participation of water is obtained.
The initial glass material is preferably an amorphous medium containing an amount of crystalline phase is not recorded by an X-ray method. Fig. 3 shows the XRD spectrum of the tested glass, whose form is characteristic of the X-ray amorphous material.
Under dispersing the porous structure of the sample is actively destroyed, it increases the degree of sample's amorphousness. Degree of amorphous suspension (Fig. 4, line a) is greater than the sediment (Fig. 4, line b). Synthesis of new crystalline phases in this sample isn't detected.
EMR spectra (electronic magnetic resonance) registered on EPR - spectrometer X-band SE/X-2544. EMR spectrum of initial ceramic foam sample is represented by line of complex shape which is formed by magnetic centers in the sample, which lines are overlapped with each other. Spectra simulation has allowed to allocate the three centers (Fig. 5). Paramagnetic (phase I), paramagnetic phase is formed apparently by iron salts. Parameters: g-factor = 1,8; linewidth AH = 46 mT. Phase II - magnetite (spinel) with parameters g = 2,13; AH = 108 mT. Hematite (phase III)) - g = 3,3; AH = 128 mT.
(w
1fo
3 130 00
«H
4t>
Fig. 3. XRD spectrum of the initial glass material powder
W _ _ TO 20
№
Tarn 60
40' 30-sola
□ \a no aa to so
Fig. 4. XRD spectrum of glass material after dispersion (a - suspension, b - sediment)
Difference in g-factors values of considered phases from listed in [13] caused by complex structure of the ceramic foam that is also observed in other studies [14]. Obtained from EMR data on the magnetization in arbitrary units (given in brackets) allow determining the contribution to the magnetism of these phases (for the degree of increase): III (5177) - I (8567) - II (9472).
After dispersing the restructuring of the paramagnetic component ceramic foam associated possibly with change of iron valence is fixed by EMR spectra of sediment. Spectra simulation (Fig. 6b) allows to select the line with the parameters g = 2,02; AH = 79) mT, which value the same with the values of g and AHfor magnetite particles [14] and the line g = 21>; AH = 100 mT (hematite).
The temperature behavior of sedimenl magnetization is typical for samples superparamagnetic nanoparticles (Fig. 6a). With decreasing temperature, the lines displaced in lower field, the width
decreases. This can be related to increasing exchange interaction, narrowing line (Lorentz line shape) or structural changes. So for magnetite (phase II) at 293 K the magnetization value per unit is equal to 41112, at 77-10475, respectively. Hematite (phase III) at 293 K - 33800, at 77-15377, respectively. A sharp drop in the magnetization of hematite shows greater magnetic permeability for these particles compared with magnetite particles. The line broadening after dispersion can be related to an increase in the contribution of surface heterogeneity with decreasing particle size, or increasing the dimensional dispersion. The values of g-factors also a bit changed for these reasons.
Analysis of the EPR spectra of the initial sample glass material showed that it has a structure with a developed surface, contains manganese oxides (line 1, Fig. 7) and iron (low-field part of the spectrum, line 2, Fig. 7). The fraction containing manganese quantitatively dominates. Line parameters 1 at 293 K: g = 2,0075; AH = 49,2 mT. Temperature reduction to 77 K leads to a line shift in the lower field g = 2,015 and the broadening of the line to 62 mT. State of iron complexes is paramagnetic - signal increased with decreasing temperature, g-factor equal to 4,54, typical for low-symmetric state of iron.
After grinding the sample (sediment) contains manganese oxide (line 1, Fig. 8). Line parameters have changed slightly: g = 2,013, AH = 50,4 mT. Iron component in the EPR spectrum is almost unnoticeable. The component containing iron, it is shifted to lower field: g = 4,54 (line 2, Fig. 8) prevails in suspension EPR spectrum.
The manganese oxide is in much smaller amount than in the initial sample (line 1a, Fig. 8). Line parameters have changed: g = 2,038, AH = 53 mT, it can be associated with increasing in particle fineness and surface changing. Thus, as a result of glass material grinding accompanied by cavitation enrichment effect is observed: phase manganese prevails in the sediment, and iron phase in suspensions.
Mossbauer spectra were measured with a source Co57 (Cr) on the ceramic foam before and after the dispersion are shown in Fig. 9. Spectra represent the sum of several Zeeman sextets and quadrupole doublets caused by different states and positions of iron.
Probability of the hyperfine fields in the experimental spectrum, defined for differeni valence states of iron, show a wide the field distribution near she 5 10 and 470 kOe for Fe3 + with a characteristfc chemical shift value of ~ 0.3 mm/s and near 4410 kOe Fe2>5 + with a characteristic chemicyl sWft value
Fig. 7. EPR spectra of the glass material initial sample
Fig. 8. EPR spectrum of sediment and glass material suspensions after dispersion
o -i—' _q
o
isi
_q
Initial ceramic foam
V J* *..,/ / * + *
sediment after : W
dispersion V y . f \ V
./y * ++ A v ; WV / * + ** * . * *. • V
-10 -s o 5 10
rate, mrn/s
Fig. 9. Mossbauer spectra of the initial ceramic foam and sediment samples
of ~ 0,7 mrn/s. The appearance of mixed valence iron indicates that the sample contains magnetite. Deviation of the values of the hypeifine fields of 490 and 460 kOe inherent to stoichiometric magnetite indicates magnetite defects. Fitting model spectrum consisting of four sextets and two doublets to the experimental spectrum leads to Mossbauer parameters shown in Table 1.
Mossbauer spectroscopy results have shown that the samples contain three iron phases: hematite, magnetite and paramagnetic phase. Hematite phase has hyperfine field of ~ 510 kOe, which is less than 517 kOe in stoichiometric hematite. This decrease of the field probably related to the dilution of hematite by aluminum contained in the initial ceramic foam.
In the magnetite phase (spinel) identified tetrahedral positions Fe3 + (A) and octahedral positions Fe3 + (B) and Fe2,5 + (B), in contrast to the stoichiometric magnetite, which are observed only two sextet: Fe3 + (A + B) with a typical field H = 490 kOe and Fe2,5 + (B) with a typical field 460 kOe. Initial ceramic foam contains appreciable amounts of CaO and Al2O3. Calcium and aluminum cations are capable of entering into the spinel lattice, thus Ca2 + prefers tetrahedral and Al3 + - octahedral spinel.
Table 1. Mossbauer parameters of iron cations in the samples of the initial ceramic foam and after dispersion (sediment)
IS, mm/s ±0,01 H, kOe ±3 QS, mm/s ±0,02 W, mm/s ±0,02 S, ±0,03 Phase
Initial ceramic foam 0,35 510 -0,44 0,26 0,03 a-Fe2O3
0,28 476 -0,10 0,45 0,13 Fe3+(A)
0,36 443 -0,37 0,93 0,18 Fe3+(B)
0,69 437 0 1,08 0,38 Fe25+(B)
0,28 0 1,33 0,78 0,16 Fe3+
0,97 0 1,98 0,95 0,12 Fe2+
Ceramic foam after dispersion (sediment) 0,36 511 -0,49 0,30 0,05 a-Fe2O3
0,30 475 -0,04 0,54 0,17 Fe3+(A)
0,56 447 -0,22 0,66 0,19 Fe3+(B)
0,58 415 0 1,36 0,33 Fe2-5+(B)
0,29 0 1,31 0,77 0,15 Fe3+
1,03 0 2,01 0,89 0,10 Fe2+
IS - isomer chemical shift relative to a-Fe, N - hyperfine field at the iron nucleus, QS - quadrupole splitting, W - width of the absorption line, S - lobar population position.
This diamagnetic dilution of magnetite decreases the values of the hyperfine fields at the positions of the spinel and wide distribution of the fields due to the occurrence of non-equivalent positions of iron on the number of magnetic neighbors.
Cations Fe3 + and Fe2 + are found in the paramagnetic phase ceramic foam. Probably the paramagnetic phase formation is an aluminosilicate containing iron in two valence states.
Spinel formation by dispersing doesn't experience any changes. There is only a decrease in mixed-valence cations, Fe2,5 + and change Mossbauer parameters. This is probably due to the oxidation of magnetitethat can be the result of oxidation of the surface cations at reducing the size of spinel formation and the conversion of magnetite part to hematite.
Conclusion
Thus, studies have shown that the profound structural changes in the material occur in the process of hydrodynamic dispersion due to high energy cavitational influence. The character of changes depends on the initial state of matter. The structure of dispersible particles in the crystalline material is not similar to initial. There is not only the destruction of the initial structure, but also the formation of new crystallographic phases.
Manganese and iron in sediment and suspension of porous silica foam redistribute by grinding. The sediment contains manganese more than suspension. Potential application field of this effect is the foam exemption of transition metal impurities down to low concentrations (mass fraction %).
References
[1] Кулагин В.А., Гераськин А.Б., Кашкина Л.В., Петраковская Э.А. // Гидродинамика больших скоростей и численное моделирование: материалы III Междунар. летней научной школы. Кемерово: ИНТ, 2006. С. 135-140.
[2] Кулагин В.А., Кашкина Л.В., Стебелева О.П., Кулагина Л.В. // Вестник Международной академии наук экологии и безопасности жизнедеятельности. 2009. Т. 14. № 6. С. 238-242.
[3] Kashkina L.V., Kulagin V.A., Kulagina L.V., Stebeleva O.P. // Chemical and Petroleum Engineering. New-York: Kluwer Academic, 2010. Vol. 47. № 1-2. P. 222-234.
[4] Кашкина Л.В., Кулагин В.А., Стебелева О.П., Кулагина Л.В. // Энергетика в глобальном мире: Тезисы докладов Первого Международного научно-технического конгресса. Красноярск: ООО «Версо», 2010. С. 415-417.
[5] Kashkina L.V., Kulagin V.A., Stebeleva O.P., Likhachev D.S., Petrakovskaya E.A. // Journal of Siberian Federal University. Engineering & Technologies 3 (2011 4) 310-325.
[6] Kashkina L.V., Kulagin V.A., Stebeleva O.P., Kulagina L.V. // Journal of Siberian Federal University. Engineering & Technologies 5 (2011 4) 465-474.
[7] Демиденко Н.Д., Кулагин В.А., Шокин Ю. И. Моделирование и вычислительные технологии распределенных систем. Новосибирск: Наука, 2012. 424 с.
[8] Емельянова Т.Ю., Кашкина Л.В, Стебелева О.П. // Материалы XIII научно-практической конференции «Интеллект и наука». Железногорск. 2013, С. 15-36.
[9] Смородов Е.А., Галиахметов Р.Н., Ильгамов М. А. Физика и химия кавитации. М.: Наука, 2008. 226 с.
[10] Ивченко В.М., Кулагин В.А., Немчин А.Ф. Кавитационная технология / ред. акад. Г.В. Логвинович. Красноярск: Изд-во КГУ, 1990. 200 с.
[11] Павлов В.Ф. Физические основы технологии получения новых материалов с заданными свойствами на основе создания системы комплексного использования техногенного и нерудного сырья. Новосибирск: СО РАН, 2005. 196 с.
[12] Стебелева О.П., Кашкина Л.В., Баюков О.А., Петраковская Э.А. // Ультрадисперсные порошки, наноструктуры, материалы: получение, свойства, применение: Труды НТК VI Ставеровские чтения (Бийск). Красноярск: СФУ, 2012. С. 188-190.
[13] Noginova N., Chen F., Weaver T. and all. // J.Phys.: Condens Matter. 2007. № 19. P. 208-246.
[14] Петраковская Э.А., Исакова В.Г., Баюков О.А., Великанов Д.А. // ЖТФ. 2005. Т. 75. С. 117-120.
Гидродинамическое диспергирование кальций-алюмосиликатных материалов из техногенного и нерудного сырья
Л.В. Кашкинаа, О.П. Стебелеваа, Т.Ю. Емельянова3, Э.А. Петраковская6, О.А. Баюков6
аСибирский федеральный университет Россия, 660041, Красноярск, пр. Свободный, 79 бИнститут физики им.Л.В. Киренского СО РАН Россия, 660036, Красноярск, Академгородок, 50/38
Изучены физико-химические свойства двух кальций-алюмосиликатных материалов после измельчения в гидродинамическом генераторе роторного типа в режиме суперкавитации. Исследованы образцы - кристаллическая пенокерамика на основе зол бурых Канско-Ачинских углей и пористый стекломатериал, полученный из нерудного сырья с низким содержанием марганца. Для анализа были использованы методы РФА, ЭМР, ЯГР (эффект Мёссбауэра), оптическая микроскопия. Показано, что в процессе гидродинамического диспергирования за счет высокоэнергетического кавитационного воздействия в материалах происходят глубокие структурные изменения. Получено, что характер изменений зависит от исходного состояния исследуемого материала.
Ключевые слова: гидродинамическое диспергирование, кавитация, зола, пеноматериал, пористая стеклокерамика.
