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UDC (15).002; 620.2(15)
Doi: 10.31772/2587-6066-2019-20-3-390-397
For citation: Mishnev S. V., Shakhov V. N., Gotovko S. A., Padar V. A., Dementeva I. S. Formation features of the central layers of the alloy Fe - 3 % Si (110)[hkl] rolling textures. Siberian Journal of Science and Technology. 2019, Vol. 20, No. 3, P. 390-397. Doi: 10.31772/2587-6066-2019-20-3-390-397
Для цитирования: Мишнев С. В., Шахов В. Н., Готовко С. А., Падар В. А., Дементьева И. С. Особенности формирования текстур прокатки центральных слоев сплава Fe - 3 % Si (110)[hkl] // Сибирский журнал науки и технологий. 2019. Т. 20, № 3. С. 390-397. Doi: 10.31772/2587-6066-2019-20-3-390-397
FORMATION FEATURES OF THE CENTRAL LAYERS OF THE ALLOY Fe - 3 % Si (110)[hkl] ROLLING TEXTURES
S. V. Mishnev2, V. N. Shakhov1*, S. A. Gotovko1, 2, V. A. Padar2, I. S. Dementeva2
1 Reshetnev Siberian State University of Science and Technologies 31, Krasnoyarsky Rabochy Av., Krasnoyarsk, 660037, Russian Federation
2 Siberian Federal University 28, Kirensky St., Krasnoyarsk, 660049, Russian Federation * E-mail: shasla@mail.ru
The fields of solid-state physics, metallurgy, plastic deformation, mathematics and continuum mechanics are engaged in the studies of texturing of metals and alloys and their influence on the operational properties ofproducts. As a rule, the most significant results are expected at the interface between these sciences.
The technologies of obtaining textured materials by metal forming processes occupy a special place in the metal-working sphere. This is due to promising directions in technologies for producing semi-finished and final products with improved structure-sensitive properties, by regulating the texturing, taking into account initial crystallographic orientation of the workpiece. The first issue to note is the formation of an ideal, one-component crystallographic texture in anisotropic metallic materials. The second issue is to obtain semi-finished and final products with more specific service properties: crystallographic texture with specific predetermined components. For instance, due to the crystallographic texture, it is possible to increase the resistance of metals and alloys against corrosion and hostile environment. Considering textured materials as composite, we must note that directionally oriented crystallites with crystallographic directions relative to the laboratory direction perform as reinforced elements. The initial texture in the processing plane is especially important. The materials, which possess unique structure-sensitive properties acquired through pressure treatment, are very promising for a widespread use in the sphere of aerospace technology.
Obviously, the properties and means of their achievement are diverse and require setting a specific task. Therefore, further research in this sphere is especially promising.
The article presents the research findings, considering the effect of initial crystallographic orientation and deformation modes on the rolling texture in the central layer of Fe - 3% Si (110)[hkl] single crystals. Several groups of single crystal samples underwent rolling under laboratory conditions. The groups of samples were classified according to the final deformation rate, the ideal crystallographic orientation of the rolling plane and deflections of the ideal orientation plane direction from the rolling direction. The methodology of the experiment took into account the compression rate value during one rolling. We analyzed the results of rolling, using the radiographic method. The next step was to superimpose the radiographic data on a stereographic projection and to construct straight pole figures. The results of straight pole figures decoding revealed differences in the texture formation from the previously obtained data. The research shows the manifestation of the one-component deformation texture in the central layer.
Keywords: deformation of single crystals, crystallographic texture, standard crystallographic projection, pole figures, deformation texture.
ОСОБЕННОСТИ ФОРМИРОВАНИЯ ТЕКСТУР ПРОКАТКИ ЦЕНТРАЛЬНЫХ СЛОЕВ СПЛАВА Fe - 3 % Si (110)[hkl]
С. В. Мишнев2, В. Н. Шахов1*, С. А. Готовко1, 2, В. А. Падар2, И. С. Дементьева2
1 Сибирский государственный университет науки и технологий имени академика М. Ф. Решетнева Российская Федерация, 660037, г. Красноярск, просп. им. газ. «Красноярский рабочий», 31
2 Сибирский федеральный университет Российская Федерация, 660049, г. Красноярск, ул. Академика Киренского, 28
*E-mail: shasla@mail.ru
Вопросами исследования текстурообразования в металлах и сплавах и их влиянием на эксплуатационные свойства изделий занимаются в областях физики твердого тела, металловедения, пластической деформации, математики, механики сплошной среды, и, как правило, наиболее значимые результаты ожидаемы на стыках этих наук.
Особое место в металлообработке занимают технологии получения текстурированных материалов процессами обработки металлов давлением. Это связано с перспективными направлениями в технологиях получения заготовки и полуфабрикатов с улучшенными структурно-чувствительными свойствами за счет регулирования текстурообразованием при учете исходной кристаллографической ориентировки заготовки. Первое, что необходимо отметить, - это формирование совершенной, однокомпонентной кристаллографической текстуры в анизотропных металлических материалах; второе - получение заготовки и полуфабрикатов с более узким назначением служебных свойств - кристаллографической текстуры с определенными, заранее заданными компонентами. Так, например, за счет кристаллографической текстуры можно повысить стойкость металлов и сплавов против коррозии и действия агрессивных сред.
Рассматривая текстурированные материалы как композиционные, отметим, что в качестве армии-рующего элемента здесь выступают направленно ориентированные кристаллиты своим кристаллографическим направлением относительно лабораторного направления. Особое место при этом отведено исходной текстуре в плоскости обработки. Такие материалы с приобретенными за счет технологий обработки давлением уникальными структурно-чувствительными свойствами весьма перспективны для широкого использования в производстве аэрокосмической техники.
Естественно, что свойства и средства их достижения многообразны и определить их можно только при постановке конкретной задачи. Поэтому направления дальнейших исследований имеют большую перспективу.
В статье предложены результаты исследования влияния исходной кристаллографической ориентировки и режимов деформации на текстуру прокатки в центральном слое монокристаллов сплава Fe - 3 % Si (110)[M/j. В лабораторных условиях были прокатаны группы образцов монокристаллов. Группы образцов были классифицированы по конечной величине деформации, по идеальной кристаллографической ориентировке, лежащей в плоскости прокатки, и по отклонениям направления плоскости идеальной ориентировки от направления прокатки. Методикой проведения эксперимента учитывалась так же и величина обжатия за один подкат. Для исследования результатов прокатки был применен рентгенографический метод. Данные рентгенографического исследования накладывали на стереографическую проекцию и строили прямые полюсные фигуры. Результаты расшифровки прямых полюсных фигур выявили отличия в формировании текстуры от ранее полученных результатов. Эти отличия заключаются в проявлении в центральном слое однокомпонентной текстуры деформации.
Ключевые слова: деформация монокристаллов, кристаллографическая текстура, стандартные кристаллографические проекции, полюсные фигуры, текстуры деформации.
Introduction. The technical feasibility level of the the fields of solid-state physics, metallurgy, plastic degeneral results of fundamental scientific research is de- formation, mathematics and by leading specialists of the termined both in the field of creating new materials due to machine-building complex. Theoretical and experimental the super purity of composition, and by improving the data in the metal forming, based on the preferred orienta-internal structure during deep technological processing, in tion in micro plastic deformations, allows us to design particular - by pressure. Here, at the junction of two areas new types of textures using special schemes of the exter-of production and processing, the semi-finished products nal field of influence, based on the symmetry approach acquire unique structure-sensitive properties. [3-6]. The design of new types of textures, on a symmetry
One of the most promising areas for creating compos- basis, is aimed at obtaining semi-finished and final prodite materials with unique properties is based on the devel- ucts with predetermined structure-sensitive properties. As opment of a reinforcing element, which consists of ultra a result, it will lead to the improvement of the operational strong crystalline filaments. However, their production for properties of machines and mechanisms. use as reinforcement is possible only in space, which lim- The research problem formulation and the physi-its the field of application. cal essence of the process. The texture formation during
Texture orientation components of metallic materials, the plastic deformation is a consequence of the rotation of created under earth conditions by pressure treatment tech- crystallographic planes and directions in crystallites, rela-niques, can be considered as an alternative to crystalline tive to technological or other special directions [7]. The filaments. Due to the presence of deep anisotropy, the components of the crystallographic texture (planes and textured materials are commonly regarded as quasi-single directions) underlie the formation of structure-sensitive crystals. As a result, based on the description of structure- properties connected with the symmetry of single crystals sensitive properties for both types of the reinforcing ele- (crystallites) of a polycrystalline material. The connection ment, there is an interconnection between the symmetry between the symmetry of the material structure, the sym-of the structure and the symmetry of the anisotropy of the metry of the stress field structure (symmetry of the exterproperties [1-2]. The main types of textures today are nal influence) and the symmetry of the final properties, axial textures, conical textures and rolling textures, classi- connected by the displacement symmetry and the symme-fied according to the symmetry. try of the stress field, can be described with the use of a
The studies of metals and alloys texturing, as well as certain systematic approach based on the Shubnikov-
their influence on the final properties of semi-finished and Curie principles of symmetry, the Neumann's principle
final products, are conducted by the scientists working in (fundamental principle of physical crystallography), as
well as the Hermann-Herman's principle, which reflects the interconnection between the anisotropic material structures and its physical properties [8-11].
Due to the systematic approach to structural analysis, the structure of the initial workpiece is considered to be essential. In most cases, the structure of the initial work-piece is anisotropic with respect to the property considered in one direction or another and can significantly affect the final properties of the semi-finished and final products, especially when it comes to unique properties, for instance, magnetic ones.
One of the ways to optimize the structure-sensitive, physical and mechanical properties of semi-finished and final products made of polycrystalline materials can be accomplished by controlling the texturing. In this process, we must consider the initial crystallographic orientation of the original workpiece. For example, a feature of cold-rolled textured steel is the presence of a vivid crystalline texture. With an ideal rib texture in each crystallite, the {110} planes must coincide with the sheet plane, and the <100> axes must be directed along the rolling direction. However, in real samples, the orientation of most crystallites is different from the ideal one [12].
Thus, the task of the current work is to determine the effect of the initial (110)[hkl] texture of Fe - 3% Si single crystals on the deformation texture in the central layers during rolling with a different reduction rate. The formation of the rolling texture of the single crystals central layers in general has the similar character to those described earlier in the works [13-19].
The difference between rolling deformation of (110)[hkl] alloys on the surface and deformation of the central layers is that as a result of metal friction on the rolls: maximum stress axes rotate continuously around the transverse direction of rolling. As a result, there is a change in the slip systems involved in the deformation process. In case when the single crystal is oriented ideally relative to the (110) plane, there is a symmetric change of slip systems on the opposite surfaces. However, when this orientation is shifted towards the direction of rolling, there is an ambiguous participation of the slip systems in the deformation.
The study of the initial orientation and deformation modes influence on the rolling texture of (110)[hkl] single crystals with a deflection of 5^10° from the plane towards the direction of rolling was carried out on the example of the Fe - 3% Si alloy. Three types of samples were rolled under laboratory conditions. The first group had (110) [112] and (110) [111] initial ideal orientation, with the deflection of 8 degrees from the plane towards the rolling direction. The second group had (110) [331] and (110) [551] initial ideal orientation, with the deflection of 7 degrees. The third group had (110) [551] initial ideal
orientation with the deflection of 5 degrees.
Depending on the rolling direction (RD), one of the slip systems is active, i.e. the change of the rolling direction causes the change of the active slip system (ASS). Thus, it is important to find the boundary values of the rolling direction which lead to the change of an active slip
systems (ASS). When rolling a (110) [hkl] single crystal with a body-centered cubic lattice which is ideally oriented along the (110) plane, in the central layers of the sample, depending on the rolling direction and calculations, there will be the following slip systems: (112) [111]; (123) [111]; (011) [111].
The samples were rolled on the laboratory two-rolling mill DU0-90 with the rolls diameter of 90 mm, at room temperature. The rolling was carried out without grease lubricant. The guides were used in order to prevent the rotation of samples. The cross-section of the initial samples was 0,48^15,0 mm.
The determination of the single crystals orientation was performed on the X-ray apparatus URS-50I. The analysis was performed using the Lauegram reflection, by standard methods [20].
The study of texture was carried out by the method of direct pole figures (built by known methods) [21]. The diffractorgam survey was performed on the DRON-1 dif-fractometer in Fe - Ka radiation using the GP-2 attachment. The sample was tilted around the horizontal axis in the interval from 0 ° to 70° and rotated around the normal to the surface automatically during the survey, so that the angle of tilt was 3.5° for one turn around the normal. The dependence of the intensity of textureless powder standard (annealed in vacuum) was measured to consider the intensity changes at high tilt angles. Pole figures were built in the intensities of the standard. The 20 x 20 mm samples were cut on the guillotine shears. One-sided removal of material from the sample plane was carried out in order to determine the texture of the central layers. To accomplish this, the sample was poured with the Wood's alloy, then a given thickness layer was removed by mechanical polishing on an emery wheel. In order to remove the cold-worked layer and obtain the mirror surface of the sample, we performed the chemical polishing in H202 -80 %, H20 - 10 %, HF - 10 % solution. The exposure time in the solution was 10 ^ 15 seconds at the temperature of 80° C. The samples were immersed into the solution of chromic anhydride and washed with water immediately after polishing, to remove the products of the chemical polishing reaction.
The results of the X-ray analysis are presented in fig. 1-5. The formation of the rolling texture of the central layers of the "group 1" generally has the similar character to the one described in earlier works [22-24]. The main difference of the obtained results from the previous studies is that the orientation of the "group 1" deformed single crystals is single-component. Fig. 1, 2 show {110} straight pole figures (SPF) from the central layers of the Fe - 3 % Si alloy of the specified group, rolled with the reduction rate of 35, 55 and 85 %.
The analysis shows that orientation of Fe - 3 % Si (110) [hkl] alloy is one-component: the samples with (110) [112] ideal orientation, at the reduction rate of 35 % have the orientation close to (112) [351] (fig. 1, a); the samples with (110) [111] ideal orientation have the orientation close to (326) [661] (fig. 2, a). The latter sample also has dispersion around the transverse rolling direction.
The further increase of deformation rate reduces dispersion and almost does not change the orientation (fig. 1, b and 2, b).
The initial sample with (110) [112] ideal orientation,
at the reduction rate of 85 %, has the orientation of the plane between (112) and (111); at the same time, it is slightly shifted counterclockwise from the [110] axis and can be recorded as (234) [562] (fig. 1, c). When the sample with (110) [111] ideal orientation is deformed at the
reduction rate of 85%, (112) [110] orientation is one-
component (fig. 2, c).
The formation of (110)[hkl] rolling texture of central layers of Fe - 3 % Si alloy (groups 2 and 3), deflected along (110) plane towards the rolling direction of 7 and 5 degrees respectively, in general has a similar character with the ones described in the earlier works. The scattering of the main orientations and the appearance of other weak components determine the peculiarities of the texturing results in groups 2 and 3.
_ ±
b
а
c
Fig. 1. Straight pole figures of the central layers of the samples b, c) of Fe - 3 % Si (110) [hkl] cold rolled
alloy with the initial (110) ideal orientation; with a deflection of 8 degrees from the (110) plane towards the rolling direction; rolled on the laboratory rolling mill with the rolls diameter of 90 mm; the reduction rate: а - 35 %, (112) [351] orientation; b - 55 %, (112) [351] orientation; c - 85 %, (234) [562] orientation
Рис. 1. Прямые полюсные фигуры (110) центральных слоев образцов (а, б, в) холоднокатаного сплава Ев - 3% (1100)[НЩ с исходной идеальной ориентировкой (110), с отклонением от плоскости (110) в сторону направления прокатки на 8 градусов, прокатанных на лабораторном прокатном стане с диаметром валков 90 мм, со степенью обжатия: а - 35 %, ориентировка (112) [351]; б - 55 %, ориентировка (112) [351]; в - 85 %, ориентировка(234) [562]
b
Fig. 2. Straight pole figures of the central layers of the samples b, c) of Fe - 3% Si (110)[hkl] cold rolled
alloy with the initial (110) ideal orientation; with a deflection of 8 degrees from the (110) plane towards the rolling direction; rolled on the laboratory rolling mill with the rolls diameter of 90 mm; the reduction rate: а - 35 %, (326) [661] orientation; b - 55 %, (335) [110] orientation; c - 85%, (112) [110] orientation
a
с
Рис. 2. Прямые полюсные фигуры (110) центральных слоев образцов (а, б, в) холоднокатаного сплава Ев - 3% (110)[М/] с исходной идеальной ориентировкой (110), с отклонением от плоскости (110) в сторону направления прокатки на 8 градусов, прокатанных на лабораторном прокатном стане с диаметром валков 90 мм, со степенью обжатия: а - 35 %, ориентировка (326) [661]; б - 55 %, ориентировка (335) [110]; в - 85 %, ориентировка (112) [110]
The peculiarities of texturing are influenced by the rolling conditions and the initial crystallographic orientation of the initial samples. The results of the radiographic analysis of the rolling groups 2 and 3 are presented in fig. 3-5. The analysis of pole figures was carried out similarly to the first group. The data is presented in the table below.
Thus, in the process of formation of (110) [hkl\ rolling texture of the Fe - 3% Si alloy central layers
with the deflection of 8 degrees from (110) plane towards the rolling direction, the following results were obtained.
In all cases, the orientation appeared to be one-component; in the case of [112] initial direction, it is close to [562] direction; in the case of [111] initial direction, it is close to [110] direction.
а b c
Fig. 3. Straight pole figures of the central layers of the samples (а, b, c) of Fe - 3% Si (110)[hk/] cold rolled alloy with the initial (110) [331] ideal orientation; with a deflection of 7 degrees from the (110) plane towards the rolling direction; rolled on the laboratory rolling mill with the rolls diameter of 90 mm; the reduction rate: а - 35 %, (221) [341] orientation; b - 55 %, (790) [972] orientation; c - 85 %, orientation▲ - (111) [110], □ - (010) [100]
Рис. 3. Прямые полюсные фигуры (110) центральных слоев образцов (а, б, в) холоднокатаного сплава Fe - 3% Si (110)[М/] с исходной идеальной ориентировкой (110) [331], с отклонением от плоскости (110) в сторону направления прокатки на 7 градусов, прокатанных на лабораторном прокатном стане с диаметром валков 90 мм, со степенью обжатия: a - 35 %, ориентировка (221) [341]; б - 55 %, ориентировка (790) [972]; в - 85 %, ориентировка ▲ - (111) [110] , □ - (010) [100]
а b c
Fig. 4. Straight pole figures of the central layers of the samples (а, b, c) of Fe - 3 % Si (110)fhklJ cold rolled alloy with the initial (110) [551] ideal orientation; with a deflection of 7 degrees from the (110) plane towards the rolling direction; rolled on the laboratory rolling mill with the rolls diameter of 90 mm; the reduction rate: а - 35 %, (331) [551] orientation; b - 55 %, (331) [110] orientation; c - 85 %, (122) [0П] orientation
Рис. 4. Прямые полюсные фигуры (110) центральных слоев образцов (а, б, в) холоднокатаного сплава Fe - 3% Si (110)[hk/] с исходной идеальной ориентировкой (110) [551], с отклонением от плоскости (110) в сторону направления прокатки на 7 градусов, прокатанных на лабораторном прокатном стане с диаметром валков 90 мм, со степенью обжатия:
a - 35 %, ориентировка (331) [551]; б - 55 %, ориентировка (331) [110]; в - 85 %, ориентировка (122) [0 11]
Fig. 5. Straight pole figures of the central layers of the samples (а, b, c) of Fe - 3 % Si (110)[hkl] cold rolled alloy with the initial (110) [551] ideal orientation; with a deflection of 5 degrees from the (110) plane towards the rolling direction; rolled on the laboratory rolling mill with the rolls diameter of 90 mm; the reduction rate: а - 35 %, (332) [T10] orientation; b - 55 %, orientationA - (111) [T10]; c - 85 %, orientation ▲ - (111) [110]
Рис. 5. Прямые полюсные фигуры (110) центральных слоев образцов (а, б, в) холоднокатаного сплава Fe - 3% Si (110)[MZ] с исходной идеальной ориентировкой (110) [551] , с отклонением от плоскости (110) в сторону направления прокатки на 5 градусов, прокатанных на лабораторном прокатном стане с диаметром валков 90 мм, со степенью обжатия: а - 35 %, ориентировка (332) [110]; б - 55 %, ориентировка ▲ - (111) [110]; в - 85 %, ориентировка ▲ - (111) [110]
Radiographic analysis of the Fe - 3 % Si alloy rolling groups 1-3
Group Figure Initial ideal orienta- Deflection from (110) plane [degrees] Orientation after deformation, %
tion 35 55 85
Preliminary Intermediate Final
1 1 (110) [Ï12] 8 (112) [351] (112) [351] (234) [562]
2 (110)[Y11] 8 (326) [661] (335) [110] (112) [110]
2 3 (110)[331] 7 (221) [341] (790) [972] (111)[110] (010)[100]
4 (110) [551] 7 (331) [551] (331)[110] (122) [011]
3 5 (110)[551] 5 (332) [110] (111)[П0] (111)[П0]
The analysis of texturing during the rolling process of single crystals of groups 2 and 3 showed that there is a similarity in texture formation. The main orientation in all the cases is (111) [110], i. e. the single crystal rotates around [110] crystallographic direction, close to the direction of rolling.
The difference between the analysis results concerning the alloys of groups 3 and 2 is the following: in the first case, a one-component (111) [110] orientation is formed, while in the second case almost always there is another weak orientation. It must be noted, that a one-component (111) [110] orientation is formed in case of a small reduction rate during one rolling, whereas an increase in reduction leads to a two-component orientation.
Conclusion. The crystallographic texture determines the service structurally dependent properties of crystalline materials and contributes to the achievement of an opti-
mum level of physical and mechanical properties. During cold rolling, the crystal lattice is reoriented throughout the entire volume of the single crystal. The geometry of it depends on the initial orientation and the active slip system, determined by the Schmid's factor, the maximum value of which reaches 0.5.
It must be noted that during rolling, the texture of the central layer of group 1 single crystals is described by a single-component orientation. When the (110) plane deflects by an angle 9 = 8°, the Schmid's factor (S) for the slip system (123) [111] - S1 = 0.46 is larger than
for the slip system (213) [111] - S2 = 0.38. As a consequence, the active slip system is (123) [111], which leads to the appearance of one-component orientation (234) [562] in the central layers, deflected from the rolling
plane around the transverse rolling direction, due to the action of symmetric slip systems.
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© Mishnev S. V., Shakhov V. N., Gotovko S. A., Padar V. A., Dementeva I. S., 2019
Mishnev Sergey Vasil'evich - Cand. Sc., associate professor of the department Mechanical; Siberian Federal University, Polytechnic Institute. E-mail: smishnev@sfu-kras.ru.
Shakhov Viacheslav Nikolaevich - the senior lecturer of the department Welding of aircraft; Reshetnev Siberian State University of Science and Technologies. E-mail: shasla@mail.ru.
Gotovko Sergey Alekseevich - Cand. Sc., associate professor of the department Mechanical, Siberian Federal University, Polytechnic Institute; associate professor of the department Welding of aircraft; Reshetnev Siberian State University of Science and Technologies. E-mail: gefest_61@mail.ru.
Padar Valerii Aleksandrovich - Cand. Sc., associate professor of the department Mechanical; Siberian Federal University, Polytechnic Institute. E-mail: va_padar@mail.ru.
Dementeva Irina Sergeevna - the senior lecturer of the department Mechanical; Siberian Federal University, Polytechnic Institute. E-mail: irene.dementyeva@gmail.com.
Мишнев Сергей Васильевич - кандидат технических наук, доцент кафедры машиностроения; Сибирский федеральный университет, Политехнический институт. E-mail: smishnev@sfu-kras.ru.
Шахов Вячеслав Николаевич - старший преподаватель кафедры сварки летательных аппаратов; Сибирский государственный университет науки и технологий имени академика М. Ф. Решетнева. E-mail: shasla@mail.ru.
Готовко Сергей Алексеевич - кандидат технических наук, доцент кафедры машиностроения, Сибирский федеральный университет, Политехнический институт; доцент кафедры сварки летательных аппаратов, Сибирский государственный университет науки и технологий имени академика М. Ф. Решетнева. E-mail: gefest_61 @mail.ru.
Падар Валерий Александрович - кандидат технических наук, доцент кафедры машиностроения; Сибирский федеральный университет, Политехнический институт. E-mail: va_padar@mail.ru.
Дементьева Ирина Сергеевна - старший преподаватель кафедры машиностроения; Сибирский федеральный университет, Политехнический институт. E-mail: irene.dementyeva@gmail.com.
