TEKA. COMMISSION OF MOTORIZATION AND ENERGETICS IN AGRICULTURE – 2013, Vol. 13, No.4, 218-224
Properties of the phase components of the modified cement system
Dmytro Rudenko
Volodymyr Dahl East-Ukrainian National University, Molodizhny bl., 20ɚ, Lugansk, 91034, Ukraine, e-mail: [email protected] Received September 18.2013: accepted October 09.2013
S u m m a r y : The article presents the results of the properties. The simplest way of intensification study of the influence of modification on the clinker of hydration process and optimization of mono minerals structure formation. A research of synthesized and modified mineral systems resistance to cement systems structure formation is a usage the weathering (carbonation, varying conditions), as of polyfunctional admixtures [5, 11, 16, 19, well as to the aggressive solutions exposure was 23]. Such additives, intensifying hydration conducted. process, having an effect on the hydration K e y w o r d s : cement system, modification, mono products morphology and their structure minerals, resistance. formation process, can’t be composed of one component [15, 27, 28, 30]. Obviously, such INTRODUCTION additives must form a complex with polyfunctional properties. At the same time, There are many ways of purposeful organic plasticizers, widely used at building control of structure formation of the concrete industry enterprises, require an addition with mixtures’ cement systems at different stages of special mineral components, chemically hardening [1, 3, 6]. The most rational way is a interacting with clinker minerals. Thus, it’s structure adjustment through the introduction necessary to choose a complex composition of modifiers. Modification of cement systems modifier with polyfunctional effect on the by various chemically-active components structuring cement system. An optimizing intentionally changes hardening and structure effect of the complex modifier becomes formation processes, provides the apparent on the crystallochemical level of improvement of the technological properties of structure formation. Consequently, the material [2, 4, 7-9]. However, modification crystallochemical optimization of the cement has an ambiguous impact on the properties of systems structure formation may be performed mono minerals of the cement system [12, 13, by a special complex, based on modern non- 21, 22, 26]. deficit and effective components [10, 17, 18]. Modification means creation of favorable Nowadays there are many ways of conditions for the clinker minerals chemical modification of binding systems, most of them interaction and further formation of the based on the turbulent mixing of components. concrete cement matrix with specified At the turbulent motion material particles PROPERTIES OF THE PHASE COMPONENTS OF THE MODIFIED CEMENT SYSTEM 219 move randomly both in the direction of current RESEARCH DATA and transversely to it. The particles interpenetrate from one layer to another, the Study of the property change of the number of their encounters increase [14, 19, phase components of the modified cement 20, 24]. system during six months carbonation shows Usually abroad turbulent mixing is used that the bending strength of both, hydrated for the preparation of injection compositions, calcium silicate (tobermorite group) and as they help to raise the stability of concrete xonotlite, diminishes, whereas on the contrary mixtures. the strength of the highly basic hydrated In the authors’ opinion, turbulent mixing calcium silicate significantly increases (Table leads to the deflocculation of a cement-water 1). In this conditions low-basic hydrosilicates, suspension, as a result saturation of suspension especially tobermorite group, despite their with colloid particles increase, the paste higher density, carbonate much faster and becomes more stable, bleeding reduces. As a change more intensively in comparison with result of turbulent mixing, cement paste the less dense highly basic hydrated calcium viscosity decreases to a certain point in time, silicate. when the mixture temperature rise due to the Table 1. Operating abilities of modified monomineral exothermal reaction of clinker minerals systems hydration starts acting back and the mixture Bending resistance, MPa thickens. The optimal duration of mixing, after Phase when paste viscosity decreases with the after after alternate components simultaneous reduce of bleeding, is in a certain synthesis carbonation wetting and drying relationship to a water-cement ratio [10, 17, C–S–H(I) 8,0 9,3 8,6 18, 25]. Xonotlite 14,3 11,6 10,2 The authors [18, 23] are of opinion that ɋ2SH(A) 4,5 5,9 6,6 turbulent treatment leads to an increase of the C2SH(C) 2,8 4,8 5,4 C3AH6 4,4 6,2 5,6 cement specific surface area due to the grinding of fine fraction. However, the results C3ASH4 3,9 5,7 6,3 Degree of of the research conducted by authors [10, 29, Bending resistance, MPa Freeze- shrinkage thaw 30] showed that specific surface area remains in 5% in 2,5% after resistance, unchanged. Hence, contradictoriness of solution of solution of carbonation, cycles opinions is indicative of insufficient Na2SO4 MgSO4 % knowledge of binding systems modification. 7,6 6,7 54 2,4 12,9 9,6 47 0,93 An ambiguous impact of different modifiers 4,4 2,5 275 0,52 on clinker mono minerals should also be taken 3,6 2,7 154 0,34 into account, as in bulk this may have a Fractures in Fractures in - 0,21 17 days 26 days negative impact on the processes of structure Fractures in Fractures in - 0,12 formation of the concrete cement matrix. 46 days 57 days
PURPOSE The reason of it is a big specific surface area of C–S–H(I), which accelerates its The purpose of the work is a research of interaction with carbonic acid gas and leads to synthesized and modified mineral systems a fast oversaturation and occurrence of a big resistance to the weathering (carbonation, number of nuclei. A lot of small defective varying conditions), as well as to the crystals emerge as a result. Besides, the aggressive solutions exposure. significant carbonation speed of low-basic hydrated calcium silicate (tobermorite group) can be explained by its layer structure. Access of moisture-dissolved carbon acid gas inside the hydrated calcium silicate 220 DMYTRO RUDENKO takes place together with hygroscopic water observed in the process of carbonation of when a water molecule penetrates along the calcium hydrosilicate, besides the chemical layered crystal cleavage surface. The processes listed above. The intensity of stress carbonation speed of hydrated calcium silicate and its tension seem to raise with the increase to a great extent depends on the humidity of of carbonation speed. environment. At the same time, ions of ɋɚ2+ in Study of changes of the hydrated calcium hydrosilicate, being a center of water molecule aluminate and calcium hydrogarnet properties persorption according to the two types of a showed that when artificially carbonated the bond (silicon-oxygen radicals and Ɉɇ- ions) in hydrated calcium aluminate strength increases a crystal cell, take carbon acid gas much in a greater degree than calcium hydrogarnet - easier. If ɋɈ 2 is replaced according to Ɉɇ strength. Judging by the amount of the bonds, then ɋɚɋɈ 3 forms instead of combined ɋɈ2 this corresponds to a significant hydrosilicate, and if the replacement takes degree of carbonation of hydrated calcium place according to the silicon-oxygen radicals aluminate in comparison with calcium bond, then scawtite forms. It should be hydrogarnet. In the conditions of alternate mentioned that in the usual terms replacement wetting and drying during 50 cycles the of ɋɈ2 takes place according to the ionic bond strength of tobermorite group and xonotlite - Ɉɇ . decreases and the strength of C2SH(A) and It is established that modified concrete C2SH(C) increases, but in a lesser degree than strength and deformability change differently at carbonation (Table 1). In these conditions depending on the concentration of carbon the strength of hydrated calcium aluminate dioxide in the atmosphere. In the first case, almost doesn’t change and the strength of when the concentration of ɋɈ2 is weak, i.e. the calcium hydrogarnet increases slightly. Along oversaturation of the solution is not too big, with this an imperceptible shrinkage is calcite crystallizes calmly and its crystals are observed. larger. Calcite crystals grow due to the joining The layered structure and water of atoms near the active centers, calcite has contained in the structure of hydrated calcium better structural properties (less defect and silicate (tobermorite group) are able to change dislocation cluster). depending on the effect of environment. If we In the second case, when the ɋɈ 2 consider a layered crystal of tobermorite as concentration is strong and the oversaturation compiled packages connected along the basal is significant and even exceeds a critical value, planes of the elementary crystallites than calcite crystallization takes place in a abrupt change of desorption curves is due to spontaneous formation of nuclei, small crystals exudation of hygroscopic water from the of the same size form for a certain period of interplanar spacing. At the same time a unit time. Therefore, to improve the structure and cell ɫ parameter changes from 27 to 24,6. 10-10 m properties of the crystals of calcite, which is [5, 12, 15]. one of the products of hydrated calcium Properties of hygroscopic water in silicate carbonation, it’s necessary to reduce hydrated calcium silicate with layered oversaturation, i.e. to reduce the concentration structure depend on H2O/SiO2 ratio. When the of the carbonized environment. ratio value is less than one then molecules of The strength of the carbonated calcium hygroscopic water are not included in the hydrosilicate is determined by the degree of structure of the crystal lattice and have a crystallization and the size of crystals. In the mobility of liquid water and so the water is process of carbonation of a less crystallized inconstant due to the environment factors C–S–H(I) a large amount of loose calcium variations [6, 22]. carbonate is formed. It is established that when silica- A physical phenomenon, accompanied containing component is introducted in the by bulking of a solid phase, and bringing forth amount more than 20% of cement weight then the inherent stresses in concrete can be new phases form, and if the amount is less the PROPERTIES OF THE PHASE COMPONENTS OF THE MODIFIED CEMENT SYSTEM 221
20% then there is a replacement of ions in the calcium silicate, such as xonotlite and crystal lattice of the cement phase C2SH(C). Although the shrinkage of the latter components. The ability of the cement phase is high, however it can be minimized by 3+ 3+ 2- components to replace isomorphously the ions substituting ions of Al , Fe and SO4 in of other elements in their lattices varies their lattice. Beneficial effects are caused by 3+ 3+ 2- according to the type of a mineral modifier, the fact that ions of Al , Fe , SO4 are in the the similarity of its physical and chemical structure of hydrated calcium silicate, characteristics and atomic size with the cement substituting Si4+, and Fe3+ hardly gets in the phase components. We have studied the crystal structure due to the large ionic radius in processes of substitution of ions of Na+, Al3+, comparison with Si4+ [27]. The replacement 3+ 4- 2- 3+ Fe , SO 2 and CO3- by the hydrated calcium of Fe has a more beneficial effect on the silicate and the change of the properties of the shrinkage of xonotlite and C2SH(C) which are latter during carbonation. It is established that synthesized at higher ratio of CaO/SiO2, than the optimal amount of mineral modifier, by the C–S–H(I). degree of substitution and its positive The study of the corrosion stability of the influence on the properties of hydrated phase components of the modified cement calcium silicate, varies depending on the ratio system in sulphate solutions within 12 months ɋɚɈ/SiO2 in the mixture and intensity of showed that the most intensive fracture of modification. hydrated calcium silicate can be observed ian The positive effect of substitution of MgSO4 solutions. In this solution in the initial these ions on the properties of the cement period of storage (up to 3 months) the strength phase components can be estimated to a large of the samples increases, in the sequel it extent by the degree of shrinkage behavior reduces. The strength in Na2SO4 solution starts after carbonation of the hydrated calcium reducing from the initial period of storage. silicate. It is established that that the major Low-basic hydrated calcium silicate part of the shrinkage of C–S–H(I) takes place (tobermorite group and xonotlite) corrode on the first 5…10 days, shrinkage of the more in the sulphate of magnesia solutions, tobermorite on the 20…25 days, xonotlite and than highly basic hydrated calcium silicate C2SH(C) on the 10…20days. Depending on [C2SH(A) ɢ C2SH(C)]. After one year storage the type of modifier shrinkage processes of the in a 2,5% solution of MgSO4 their resistance hydrated calcium silicate proceed in varying coefficient decreases to 0,76…0,68. + degrees. So, for example, replacement of Na The increased corrosive action of MgSO4 reduces shrinkage of C–S–H(I) up to 4 times, solutions on hydrated calcium silicate in tobermorite and C2SH(C) almost up to 1,5 comparison with Na2SO4 solutions is due to times. In these conditions replacement of ions the fact that ions of the latter because of the of Al3+ reduces the shrinkage of C–S–H(I) and heterovalent substitution by the scheme tobermorite up by 10…20%, xonotlite up to 2NA+ļCa2+, as well as the difference in their 1,5 times, C2SH(C) up to more than 2,5 times. ionic radii complicate their interaction, while 2- 2- 2+ 2+ Replacement of CO3 and SO4 is conductive the substitution Mg ļCa between cations to the significant reduction of shrinkage, Mg2+ and Ca2+, which have closer ionic radii, especially in tobermorite and xonotlite – up to goes on faster. Reactive capacity of the 2 times, in C2SH(C) almost up to 1,5 times. specified solutions with hydrated calcium Analysis of the data shows that selection silicate is also determined by the adsorption of the type and the degree of substitution of capacity of their ions. So, polyvalent cations of ions allows reducing the shrinkage of hydrated Mg2+ are better adsorbed in hydrated calcium calcium silicate extensively. Especially it silicate than monovalent cations of Na+. This refers to hydrated calcium silicate C–S–H(I) can be explained by Pyeskov-Fajans rule: and tobermorite, which have a significant when hydrated calcium silicate interreacts with shrinkage, their shrinkage can be brought to MgSO4 solution, all the occurring products the level of low-shrinkage type of hydrated (MgSO4 and gypsum) are hardly soluble, 222 DMYTRO RUDENKO
whereas with Na2SO4 solution only gypsum is i.e. on the diffusion coefficient of the particles hardly soluble and the second type of the interacting through the film. reaction product NaOH is in the liquid phase. The analysis showed that interfacial Furthermore, in these conditions adsorbability films formed at the interaction of C2SH(A) and 2+ - of the cations of Mg , which form with Ɉɇ C2SH(C) with sulphate solutions (Na2SO4 and ions less soluble Mg(OH)2 ( water solubility at MgSO4) have a dense structure and when 20ºɋ makes 0,9 mg/l), is more than tobermorite group and xonotlite interact with 2- adsorbability of SO4 ions, which form the specified solutions they , on the contrary, gypsum with cations of ɋɚ2+ (its water have a porous structure. It means that ions of solubility makes 2,41 mg/l). xonotlite, tobermorite, C–S–H (I) and From this it follows that a double electric interacting solutions can freely diffuse through layer is formed on the border of hydrated them. calcium silicate and the specified solutions, Thus, the formation of a porous film in and in MgSO4 solution a double electric layer the 2,5% solution of MgSO4 is one of the on the surface of hydrated calcium silicate is reason of such a fast fracture of low-basic formed from the ions of Mg2+ and Ɉɇ-, and in hydrated calcium silicate. But, despite this 2+ Na2SO4 solution from the ions of ɋɚ and they fracture more slowly in a 5% solution of 2- SO4 . The speed of the electric double layer Na2SO4 that is the consequence of the less formation depends on the adsorption capacity reacting capacity of the ions of Na+, than of of the ions of solutions, and this determines Mg2+. the intensity of the corrosive processes. Considering the kinetics of cement phase components interaction with aggressive CONCLUSIONS solutions it may be said that chemical 1. Based on the above we can conclude heterogeneous reaction rate is determined by that highly basic hydrated calcium silicate in the interacting particles diffusion rate. As a solutions of MgSO and Na SO must fracture result of interaction of the hydrated 4 2 4 slower or slightly lose its original strength due components of cement with the corrosive to the protective film. In fact, in MgSO environment an interfacial film occurs, it has 4 solution that's the way it is and in Na SO different density depending on the ratio of a 2 4 solution, on the contrary, highly basic hydrated volume of reaction products and reacting calcium silicate fractures intensively. substances. This film, consisting of a mixture 2. Such inconsistency of the mechanism of CaSO ·2H O, Mg(OH) and gel SiO , 4 2 2 2 of Na SO solution on the highly basic inhibits or in some cases neutralizes the rate of 2 4 hydrated calcium silicate is due to the fact that heterogeneous reaction between the binding the resulting corrosion products are reactive to material and liquid corrosive environments if each other. the condition of continuity according to the 3. So, the presence of NaOH in the rule of Pming and Betwarts is satisfied [10]. liquid medium complicates the formation of According to this rule the molecular volume of gypsum crystals and their intergrowth with the mixture of CaSO ·2H O, Mg(OH) and gel 4 2 2 each other and dissolving in it, they form SiO must be more than the volume of binding 2 porous, available for ionic diffusion interacting materials spent on the formation of the particles. Besides, sodium hydroxide partially molecules of these compounds. Otherwise, the transfers SiO gel into soluble sodium silicate. film created by the molecules of these 2 This allows generating a protective film whose corrosion products is not enough to cover with volume is larger than the raw the solid layer the entire surface of binding materials, as a result it is loose and porous. Consequently, protective properties of the film depend on its quality (density and continuity), PROPERTIES OF THE PHASE COMPONENTS OF THE MODIFIED CEMENT SYSTEM 223
REFERENCES //Proceeding of the 7th International congress on the Chemistry of Cement. - Vol. 4. – 493-495. 1. Berger R.L., 1972.: Influence of admixtures on 13. Ogawa K., Uchikava H., Takemoto K., 1990.: the morphology of calcium hydroxide formed The mechanism of the hydration in the system during tricalcium silicate hydration //Cem. C3S portland // Cement and concrete research. – Concr. Res. – Vol. 2. – 43-55. Vol. 10. – 17-23. 2. Bernsted J., 1983.: Further Aspect of Setting 14. Olson G.ȿ., 1998.: Dɟr ȿinflus der Temperature of Portland Cement / J. Bernsted // Silicat ind. – auf Erhartung von Beton / G.ȿ. Olson // V. 48. – N 9. – 167-170. Betonstein – Zeitung. – Jg. 24. – ʋ 3. – 89-96. 3. Brunauer S.M., 1973.: Hardened portland 15. Powers Ɍ.ɋ., 1957.: Ɍhe physical structure of cement paste of low porosity. Further remarks Cement and Concrete / Ɍ.ɋ. Powers // TSJ-ACI. about early hydration. Compositions and surface – Vol. 17. – ʋ 5-6. – 189-202. area of tobermorite gel. Summary /S.M. 16. Punagin V.V., 2010.: Nonrigid properties of Brunauer, Y. Skalny, I. Odler, M. Yudenfreund modified fine grain concrete for the groiting of //Cem. Concr. Res. – Vol. 3. – 279-293. damaged structures//Herald of Volodymyr Dahl 4. ɋzernin W., 1998.: Einige Bemerkungen uber East Ukrainian National University. – ʋ 3 Verhalten der Zementen bei Damfbehandlung / (145). – 181-186. (in Russian). W. ɋzernin // Betonstein – Zeitung. – Jg. 84. – 17. Punagin V.V., 2010.: Peculiarities of the ʋ 3. – 98-103. monolithic concrete curing at the construction of 5. Daimon M., 1972.: Assembly of a vapor high-rise buildings at elevated adsorption apparatus and its application to the temperatures//Herald of Volodymyr Dahl East determination of the pore size distribution of Ukrainian National University. – ʋ 12 (154). – hydrated cement / M. Daimon, R. Kondo // Part 2. – 159-166. (in Russian). Nippon Kagaku, Tokyo. – 238-243. 18. Punagin V., 2010.: Properties and Technology 6. Jost K.N., 1984.: Relation between the Crystal of Concrete for high altitude monolithic Structures of Calcium Silicates and their construction//TEKA Kom. Mot. I Energ. Roln. – Reactivity against Water / K.N. Jost, B. Zimmer Lublin: OL PAN. – Vol. XB. – 114-119. // Cem. and Concr. Res. – V. 14. – 177-184. 19. Punagin V., 2012.: Physicochemical 7. Kim Nam-Ho, 1997.: Interaction between Characteristics of Bond and Friction between Gypsum and C-S-H phase in C3S Hydration the Modified Concrete and Sliding Formwork using ESCA /Kim Nam-Ho, Lee Young-Jin, Um for the Construction of High-rise Woo-Sik, Lee Hee-Soo //Proceedings of the Buildings//TEKA Kom. Mot. I Energ. Roln. – 10th International Congress on the Chemistry of Lublin: OL PAN. – Vol. 12. – No. 4. – 229-234. Cement. – 127-134. 20. Reading T.J., 1987.: Shotcrete as a construction 8. Marfil S.A., Maiza O.J., Bengochea A.L., material / T. J. Reading // Shotcreting. – Sota J.D., 1988.: Relationships between SiO2, Publication SP-14. – ACI. – 98-118. Al2O3, Fe2O3, CaO, K2O and expansion in the 21. Rio A., Celani A., Saini A., 1970.: New determination of the alkali reactivity of basaltic investigations on the action mechanism and on rocks //Cement and Concrete Research. – Vol. the gypsum and calcium chloride influence on 28. – Issue 2. – 189-196. the structural and mechanic characteristics of the 9. Middendorf B., 2006.: Nanoscience and hydrosilicates get out from the C3S hydration nanotechnology in cementitious materials / //II Cemento 67, N.S. – 1970. – Vol. 1. – 17-26. Middendorf B., Singh N. B. // Cement 22. Cong X., 1992.: Role of Silica Fume in International. – ʋ 4. – 80-86. Compressive Strength of Cement Paste, Mortar 10. Nevill A.M., 2000.: Wlasciwosci betonu / and Concrete /X. Cong, S. Gong, D. Darwin, Nevill A.M. [wydanie 4]. – Ʉrakow – 874. S.L. McCabe //ACI Materials Journal. – Vol. 89. 11. Nonat A., Lecoq X., Gauffinet S., 1997.: – No. 4. – 375-386. Calcium hydroxide concentration on Solution: 23. Rudenko N., 2010.: The Development of parametr determining of the early hydration of Conception of New Generation tricalcium silicate and the characteristics of the Concretes//TEKA Kom. Mot. I Energ. Roln. – products //Proc. of the X International Congress Lublin: OL PAN. – Vol. XB. – 128-133. on the Chemistry of Cement. – Geteborg. – Vol. 24. Schiller K.K., 1991.: Mechanical Properties of 2. – 50-55. Non-Metallic Brittle Materials / K. K. Schiller // 12. Odler L., 1981.: Interaction between Gypsum Cement and Concrete Research. – Vol. 2. – 35- and the C-S-H Phase Formed in C3S Hydration 42. 224 DMYTRO RUDENKO
25. Shayan A., 1992.: Microscopic Features of ɋȼɈɃɋɌȼȺ ɎȺɁɈȼɕɏ ɋɈɋɌȺȼɅəɘɓɂɏ Cracked and Uncracked Concrete Railway ɆɈȾɂɎɂɐɂɊɈȼȺɇɇɈɃ ɐȿɆȿɇɌɇɈɃ Sleepers / A. Shayan, G.W. Quick // ACI ɋɂɋɌȿɆɕ Materials Journal. – Vol. 89. – No. 4. – 348-360. 26. Stein H.N., 1992.: Thermodynamic Ⱦɦɢɬɪɢɣ Ɋɭɞɟɧɤɨ Consideration on the Hydration Mechanisms of Ca3SiO5 and Ca3Al2O6 / H. N. Stein // Cem. Ⱥɧɧɨɬɚɰɢɹ. ȼ ɫɬɚɬɶɟ ɩɪɟɞɫɬɚɜɥɟɧɵ ɪɟɡɭɥɶɬɚɬɵ Concr. Res. – Vol. 2. – 167-177. ɢɫɫɥɟɞɨɜɚɧɢɣ ɜɥɢɹɧɢɹ ɦɨɞɢɮɢɰɢɪɨɜɚɧɢɹ ɧɚ 27. Tomosawa F., 1997.: Development of a kinetic ɫɬɪɭɤɬɭɪɨɨɛɪɚɡɨɜɚɧɢɟ ɦɨɧɨɦɢɧɟɪɚɥɨɜ ɤɥɢɧɤɟɪɚ. model for hydration of cement / F. Tomosawa // ɂɫɫɥɟɞɨɜɚɧɚ ɫɬɨɣɤɨɫɬɶ ɫɢɧɬɟɡɢɪɨɜɚɧɧɵɯ ɢ Proc. of the X International Congress on the ɦɨɞɢɮɢɰɢɪɨɜɚɧɧɵɯ ɦɨɧɨɦɢɧɟɪɚɥɶɧɵɯ ɫɢɫɬɟɦ ɤ ( , Chemistry of Cement. - Geteborg. – Vol. 2. – ɜɨɡɞɟɣɫɬɜɢɸ ɚɬɦɨɫɮɟɪɧɵɯ ɮɚɤɬɨɪɨɜ ɤɚɪɛɨɧɢɡɚɰɢɢ ɩɟɪɟɦɟɧɧɵɯ ɭɫɥɨɜɢɣ), ɚ ɬɚɤɠɟ ɚɝɪɟɫɫɢɜɧɵɯ 43-50. ɪɚɫɬɜɨɪɨɜ. 28. Wrihgt James, Frohnsdorf G., 1985.: Ʉɥɸɱɟɜɵɟ ɫɥɨɜɚ: ɰɟɦɟɧɬɧɚɹ ɫɢɫɬɟɦɚ, Durability of building materials: durability ɦɨɞɢɮɢɰɢɪɨɜɚɧɢɟ, ɦɨɧɨɦɢɧɟɪɚɥɵ, ɫɬɨɣɤɨɫɬɶ. research in the United States and the influrnce of RILEM on durability research / James Wrihgt, G. Frohnsdorf // Mater. and Constr. – Vol. 18. – No 105. – 205-214. 29. Yong I.F., 1991.: Makrodefect-free Cement / I. F.Yong // A Review. Mat. Soc. – Vol. 179. – 101-122. 30. Zollo R.F., 1997.: Fiber-reinforced Concrete: an Overview after 30 year of Development / R. F. Zollo // Cem. Concr. Com. –Vol. 19. – 107-122. minimize the adverse effects of the components of commercial biocidal products on the physical and. mechanical characteristics of products. For research, we used an aqueous solution of glutaraldehyde with. an active substance concentration of 0.5 and 1 %, which was introduced into Portland cement CEM I 42.5 N. as mixing water. The degree of influence of the active substance on the properties of cement paste and. mortar was estimated according to data on heat release during hydration, strength, and phase composition. The fungicidal activity evaluation of glutaraldehyde in cement systems and the degree of their growth with. cement is also confirmed by the results of x-ray phase analysis of hardened cement at the age of 28 days. (Fig. 3). Energetically modified cements (EMCs) are a class of cements made from pozzolans (e.g. fly ash, volcanic ash, pozzolana), silica sand, blast furnace slag, or Portland cement (or blends of these ingredients). The term "energetically modified" arises by virtue of the mechanochemistry process applied to the raw material, more accurately classified as "high energy ball milling" (HEBM). This causes, amongst others, a thermodynamic transformation in the material to increase its chemical reactivity. For EMCs... The fractal analysis of the images revealed a change in the relative organization of the system, which justifiedthe nature of the change in the physical and technical properties of the modified cement composite relative to the additive-free cement composite from the perspective of self-organization. All articles published by MDPI are made immediately available worldwide under an open access license. No special permission is required to reuse all or part of the article published by MDPI, including figures and tables. For articles published under an open access Creative Common CC BY license, any part of the article may be reused without permission provided that the original article is clearly cited. Despite the improvement in mechanical properties, the cytotoxic effects of RMGICs are of more potential concern in comparison to conventional GICs, since they incorporate monomers such as HEMA along with initiators. As with composite resins, incomplete polymerization results in inadequate conversion of monomers into polymers, and these residual monomers can cause a significant cytotoxic effect when liberated into the oral environment. In addition to the components of conventional glass-ionomers, resin-modified glass-ionomer cements contain a monomer system, usually 2-hydroxyethyl methacrylate (HEMA) plus initiator. One of the ways is utilization of supplementary cementitious materials (SCMs) in the manufacture of cement and concrete. Introduction of aluminosilicate SCMs into binding mixture makes that more amount of so-called C–A–S–H phase appears in hydration products, affecting microstructure and properties of final hardened composite. Cement and cement concrete are common construction materials manufactured in large amounts. The demand for cement has been increasing for many years which is an effect of global urbanization. For example, during the decade between 2004 and 2014 above 90% increase in worldwide cement production was observed.