Vol. 24 No. 1 2022 3 EDITORIAL COUNCIL EDITORIAL BOARD EDITOR-IN-CHIEF: Anatoliy A. Bataev, D.Sc. (Engineering), Professor, Rector, Novosibirsk State Technical University, Novosibirsk, Russian Federation DEPUTIES EDITOR-IN-CHIEF: Vladimir V. Ivancivsky, D.Sc. (Engineering), Associate Professor, Department of Industrial Machinery Design, Novosibirsk State Technical University, Novosibirsk, Russian Federation Vadim Y. Skeeba, Ph.D. (Engineering), Associate Professor, Department of Industrial Machinery Design, Novosibirsk State Technical University, Novosibirsk, Russian Federation Editor of the English translation: Elena A. Lozhkina, Ph.D. (Engineering), Department of Material Science in Mechanical Engineering, Novosibirsk State Technical University, Novosibirsk, Russian Federation The journal is issued since 1999 Publication frequency – 4 numbers a year Data on the journal are published in «Ulrich's Periodical Directory» Journal “Obrabotka Metallov” (“Metal Working and Material Science”) has been Indexed in Clarivate Analytics Services. We sincerely happy to announce that Journal “Obrabotka Metallov” (“Metal Working and Material Science”), ISSN 1994-6309 / E-ISSN 2541-819X is selected for coverage in Clarivate Analytics (formerly Thomson Reuters) products and services started from July 10, 2017. Beginning with No. 1 (74) 2017, this publication will be indexed and abstracted in: Emerging Sources Citation Index. Journal “Obrabotka Metallov” (“Metal Working & Material Science”) has entered into an electronic licensing relationship with EBSCO Publishing, the world's leading aggregator of full text journals, magazines and eBooks. The full text of JOURNAL can be found in the EBSCOhost™ databases. Novosibirsk State Technical University, Prospekt K. Marksa, 20, Novosibirsk, 630073, Russia Tel.: +7 (383) 346-17-75 http://journals.nstu.ru/obrabotka_metallov E-mail: metal_working@mail.ru; metal_working@corp.nstu.ru
OBRABOTKAMETALLOV Vol. 24 No. 1 2022 4 EDITORIAL COUNCIL EDITORIAL COUNCIL CHAIRMAN: Nikolai V. Pustovoy, D.Sc. (Engineering), Professor, President, Novosibirsk State Technical University, Novosibirsk, Russian Federation MEMBERS: The Federative Republic of Brazil: Alberto Moreira Jorge Junior, Dr.-Ing., Full Professor; Federal University of São Carlos, São Carlos The Federal Republic of Germany: Moniko Greif, Dr.-Ing., Professor, Hochschule RheinMain University of Applied Sciences, Russelsheim Florian Nürnberger, Dr.-Ing., Chief Engineer and Head of the Department “Technology of Materials”, Leibniz Universität Hannover, Garbsen; Thomas Hassel, Dr.-Ing., Head of Underwater Technology Center Hanover, Leibniz Universität Hannover, Garbsen The Spain: Andrey L. Chuvilin, Ph.D. (Physics and Mathematics), Ikerbasque Research Professor, Head of Electron Microscopy Laboratory “CIC nanoGUNE”, San Sebastian The Republic of Belarus: Fyodor I. Panteleenko, D.Sc. (Engineering), Professor, First Vice-Rector, Corresponding Member of National Academy of Sciences of Belarus, Belarusian National Technical University, Minsk The Ukraine: Sergiy V. Kovalevskyy, D.Sc. (Engineering), Professor, Vice Rector for Research and Academic Affairs, Donbass State Engineering Academy, Kramatorsk The Russian Federation: Vladimir G. Atapin, D.Sc. (Engineering), Professor, Novosibirsk State Technical University, Novosibirsk; Victor P. Balkov, Deputy general director, Research and Development Tooling Institute “VNIIINSTRUMENT”, Moscow; Vladimir A. Bataev, D.Sc. (Engineering), Professor, Novosibirsk State Technical University, Novosibirsk; Vladimir G. Burov, D.Sc. (Engineering), Professor, Novosibirsk State Technical University, Novosibirsk; Aleksandr N. Gerasenko, Director, Scientifi c and Production company “Mashservispribor”, Novosibirsk; Sergey V. Kirsanov, D.Sc. (Engineering), Professor, National Research Tomsk Polytechnic University, Tomsk; Aleksandr N. Korotkov, D.Sc. (Engineering), Professor, Kuzbass State Technical University, Kemerovo; Evgeniy A. Kudryashov, D.Sc. (Engineering), Professor, Southwest State University, Kursk; Dmitry V. Lobanov, D.Sc. (Engineering), Associate Professor, I.N. Ulianov Chuvash State University, Cheboksary; Aleksey V. Makarov, D.Sc. (Engineering), Corresponding Member of RAS, Head of division, Head of laboratory (Laboratory of Mechanical Properties) M.N. Miheev Institute of Metal Physics, Russian Academy of Sciences (Ural Branch), Yekaterinburg; Aleksandr G. Ovcharenko, D.Sc. (Engineering), Professor, Biysk Technological Institute, Biysk; Yuriy N. Saraev, D.Sc. (Engineering), Professor, Institute of Strength Physics and Materials Science, Russian Academy of Sciences (Siberian Branch), Tomsk; Alexander S. Yanyushkin, D.Sc. (Engineering), Professor, I.N. Ulianov Chuvash State University, Cheboksary
Vol. 23 No. 2 2021 5 CONTENTS OBRABOTKAMETALLOV TECHNOLOGY Kuznetsov V.P., Makarov A.V., Skorobogatov A.S., Skorynina P.A., Luchko S.N., Sirosh V.A., Chekan N.M. Normal force infl uence on smoothing and hardening of steel 03Cr16Ni15Mo3Ti1 surface layer during dry diamond burnishing with spherical indenter............................................................................ 6 Gubin D.S., Kisel’A.G. Calculation of temperatures during fi nishing milling of a nickel based alloys.......... 23 EQUIPMENT. INSTRUMENTS Bratan S.M., Roshchupkin S.I., Chasovitina A.S., Gupta K. The effect of the relative vibrations of the abrasive tool and the workpiece on the probability of material removing during fi nishing grinding................. 33 MATERIAL SCIENCE OzolinA.V., Sokolov E.G. Effect of mechanical activation of tungsten powder on the structure and properties of the sintered Sn-Cu-Co-W material................................................................................................................. 48 Korobov Yu.S., Alwan H.L., Makarov A.V., Kukareko V.A., Sirosh V.A., Filippov M.A., Estemirova S. Kh. Comparative study of cavitation erosion resistance of austenitic steels with different levels of metastability................................................................................................................................................... 61 Vologzanina S.A., IgolkinA.F., PeregudovA.A., Baranov I.V., Martyushev N.V. Effect of the deformation degree at low temperatures on the phase transformations and properties of metastable austenitic steels.......... 73 Filippov A.V., Shamarin N.N., Moskvichev E.N., Novitskaya O.S., Knyazhev E.O., Denisova Yu.A., Leonov A.A., Denisov V.V. Investigation of the structural-phase state and mechanical properties of ZrCrN coatings obtained by plasma-assisted vacuum arc evaporation..................................................................... 87 EDITORIALMATERIALS Guidelines for Writing a Scientifi c Paper ............................................................................................................ 103 Abstract requirements ......................................................................................................................................... 107 Rules for authors ................................................................................................................................................. 111 FOUNDERS MATERIALS 119 CONTENTS
OBRABOTKAMETALLOV Vol. 24 No. 1 2022 TECHNOLOGY Obrabotka metallov (tekhnologiya, oborudovanie, instrumenty) = Metal Working and Material Science. 2022 vol. 24 no. 1 pp. 6–22 ISSN: 1994-6309 (print) / 2541-819X (online) DOI: 10.17212/1994-6309-2022-24.1-6-22 Obrabotka metallov - Metal Working and Material Science Journal homepage: http://journals.nstu.ru/obrabotka_metallov Normal force infl uence on smoothing and hardening of steel 03Cr16Ni15Mo3Ti1 surface layer during dry diamond burnishing with spherical indenter Viktor Kuznetsov 1, 2, 3, a,*, Aleksey Makarov 1, b, Andrey Skorobogatov 3, c, Polina Skorynina 4, d, Sergey Luchko 1, e, Vitalij Sirosh 1, f, Nikolay Chekan5, g 1 M.N. Miheev Institute of Metal Physics, Ural Branch of the Russian Academy of Sciences, 18 S. Kovalevskoy str., Ekaterinburg, 620108, Russian Federation 2 Ural Federal University named after the fi rst President of Russia B.N. Yeltsin, 19 Mira str., Ekaterinburg, 620002, Russian Federation 3 Federal State Budgetary Institution “National Ilizarov Medical Research Centre for Traumatology and Ortopaedics” Ministry Healthcare, Russian Federation, 6 M. Ulyanova st., Kurgan, 640014, Russian Federation 4 Institute of Engineering Science Ural Branch, Russian Academy of Sciences, 34 Komsomolskaya st., Ekaterinburg, 620049, Russian Federation 5 Physical-Technical Institute of National Academy of Sciences of Belarus, 10 Akademika Kuprevicha st., Minsk, 220141, Belarus a https://orcid.org/0000-0001-8949-6345, wpkuzn@mail.ru, b https://orcid.org/0000-0002-2228-0643, avm@imp.uran.ru, с https://orcid.org/0000-0001-7447-1962, ufo2log@gmail.com, d https://orcid.org/0000-0002-8904-7600, polina.skorynina@mail.ru, e https://orcid.org/0000-0002-2368-0913, serojaluchko@gmail.com, f https://orcid.org/0000-0002-8180-9543, sirosh.imp@yandex.ru, g https://orcid.org/0000-0002-3339-9922, chekan@phti.by ART I CLE I NFO Article history: Received: 15 December 2021 Revised: 03 January 2022 Accepted: 15 January 2022 Available online: 15 March 2022 Keywords: Austenitic steel Finish turning Diamond burnishing Burnishing force Roughness Microhardness Funding The research was supported by the Russian Foundation for Basic Research and the Belarusian Republican Foundation for Fundamental Research (Project No. 20-58-00057) and carried out within the state assignments of the Institute of Metal Physics, RAS (Ural Branch) on the topic No. АААА-А18-118020190116-6 and the Institute of Engineering Science, RAS (Ural Branch) on the topic No. АААА-А18-118020790148-1. Acknowledgements Research were partially conducted at core facility “Structure, mechanical and physical properties of materials” ABSTRACT Introduction. Sliding burnishing minimizes roughness and hardens of the steel surface. Quality of the formed surface and strength characteristics of the surface layer are determined by the burnishing speed, force and feed. Due to the danger of the surface micro-destruction during burnishing, the problem of selecting the favorable value of the normal force at a given feed arises. The current investigation aims to study the effect of normal force during dry diamond burnishing with a spherical indenter on smoothing the surface microprofi le and strain hardening of the 03Cr16Ni15Mo3Ti1 austenitic steel surface layer. Research methods. Profi lometry, scanning electron microscopy (SEM), microdurometry are used. Results and discussion. As the result of dry burnishing of deformation-stable austenitic steel 03Cr16Ni15Mo3Ti1 with a spherical indenter with a 2 mm radius made of natural diamond at a sliding speed of 10 m/min and feed rate of 0.025 mm/rev, it is found that in the investigated variation range of the burnishing normal force (100...200 N) the value of the smoothing coeffi cient of the initial steel surface microprofi le after fi nish turning is 79...90 %, the greatest smoothing with a decrease in the average roughness parameter Ra from 1.0 to 0.1 μm is achieved at a force of 150 N; during diamond burnishing the initial (after fi nish turning) surface is hardened by 15...43 % (up to 382...444 HV), as the burnishing force raises from 100 to 175 N, a non-monotonic increase of the average microhardness from 409 to 444 HV 0.05 takes place; burnishing with a load of 175 N forms a gradient-hardened layer with a thickness of 300...350 μm with the appearance of individual microfractures in the form of beadings and micro-cracks on the surface, the maximum hardening is caused by the formation of a highly dispersed surface layer of 30...40 μm thick with a structure of highly dispersed austenite and the corresponding activation of grain-boundary and dislocation strengthening mechanisms. The results can be used when selecting the diamond burnishing parameters of parts made of corrosion-resistant austenitic steels according to the criteria for obtaining low surface roughness without signifi cant microfractures and effective strain hardening of the surface layer. For citation: Kuznetsov V.P., Makarov A.V., Skorobogatov A.S., Skorynina P.A., Luchko S.N., Sirosh V.A., Chekan N.M. Normal force infl uence on smoothing and hardening of steel 03Cr16Ni15Mo3Ti1 surface layer during dry diamond burnishing with spherical indenter. Obrabotka metallov (tekhnologiya, oborudovanie, instrumenty) = Metal Working and Material Science, 2022, vol. 24, no. 1, pp. 6–22. DOI: 10.17212/1994-6309-2022-24.1-6-22. (In Russian). ______ * Corresponding author Kuznetsov Viktor P., D.Sc. (Engineering), Professor Ural Federal University named after the fi rst President of Russia B.N. Yeltsin, 19 Mira st., 620002, Ekaterinburg, Russia Tel.: 8 (982) 422-17-77, e-mail: wpkuzn@mail.ru
OBRABOTKAMETALLOV TECHNOLOGY Vol. 24 No. 1 2022 Introduction Austenitic stainless chromium-nickel steels, due to high level of corrosion resistance, plasticity, heat resistance, manufacturability and biocompatibility [1-3], are widely applied in the oil and gas, chemical, nuclear, food and medical industries. For many critical applications, steels of 01Сr17Ni13Mo3 type (analog AISI 316L) are of particular interest. These steels retain corrosion resistance under mechanical infl uences due to its low tendency to martensitic deformation transformation [4], and are also prospective to be used in hydrogen economy as a hydrogen embrittlement-resistant material for hydrogen transportation and storage systems [5]. Dispersion-hardening steel of Cr16Ni15Mo3Ti1 type is additionally alloyed with ~1 wt.% titanium, which provides radiationstimulated release of the coherent γʹ-phase (Ni3Ti) and thereby multiplies the resistance to void (vacancy) swelling during irradiation with high-speed neutrons at temperatures of 480...500 °C [6-9]. Therefore, it is prospective as not only corrosion-resistant, but also radiation-resistant material, operable in the presence of aggressive environments. The microhardness of non-heat-treatable AISI 316L steel surface can be increased by ultrasonic treatment with a carbide spherical indenter (from 177 to 290 HV) [10] and balls in vacuum – by SMAT: surface mechanical attrition treatment (from 1.65 to 2.90 GPa) [11], by sandblasting (from 1.8 to 3.6 GPa) [12]. However, the surface layers formed during impact hardening treatments are characterized by high roughness Ra = 1.0...2.5 μm [11, 12]. Signifi cantly more effective hardening of 03Cr16Ni14Mo3Ti1 steel surface (from 270 to 580...720 HV 0.025) can be achieved by friction treatment with a sliding indenter made of synthetic diamond in an argon medium [13]. Such processing of austenitic chromium-nickel steels can also provide high quality of the formed surface with low roughness [14, 15]. Sliding burnishing of steels minimizes roughness and strengthens the surface layer. The surface quality and strength characteristics of the surface layer formed during burnishing are determined by the speed, feed and force of burnishing, the size of the contact area and multiplicity of loading [16-23]. The paper [16] shows the possibility of controlling surface layer smoothing and strengthening based on the evaluation of the integral parameter of the multiplicity of material loading during the burnishing process. When considering diamond burnishing of stainless 17-4 PH steel, the feed is determined by the most signifi cant parameter affecting surface roughness and hardness [17]. Under conditions of dry ball burnishing, the best roughness smoothing of the turned surface of 41Cr4 steel was provided by a small feed of 0.05 mm/rev, in contrast to 0.075 mm/rev and 0.1 mm/rev [18]. On the contrary, in [19], when studying the ball burnishing of AISI 1045 steel, it was found that the greatest infl uence on both the surface roughness and hardness is exerted by the burnishing force. The normal force is also a parameter determining a high level of compressive residual stresses (-1,100 MPa) being formed by ball burnishing on the 15-5PH martensitic stainless-steel surface [20]. The depth of spherical indenter penetration (determined by normal force, microhardness and roughness of the work surface), at which complete smoothing of the initial roughness is achieved, is proposed in [21] as a criterion for ensuring minimal roughness when burnishing hardened steels and is called stable indentation. An increase in the normal force and contact spot size, as well as a decrease in the feed to increase the multiplicity of loading and hardening of the material being treated, can cause micro-destruction of the work surface. In this regard, at diamond burnishing, there is a problem of the exact assignment of the normal force at a given feed. Maximov et al. in [22] noted that there is no data in the literature on the prospects of sliding indenter burnishing of AISI 316Ti (03Cr16Ni10Mo2Ti) austenitic steel, which is closest in chemical composition to the steel under study. However, the new results obtained in [22] do not allow establishing a connection between the normal force and surface microprofi les, both after turning and after burnishing. In addition, when choosing the burnishing force, it is important to assign it from the standpoint of material strengthening. 3D surface profi lometry during the transition from turning to diamond burnishing of disks made of AISI 304 metastable austenitic steel is considered in [23]. However, the assignment of the normal loading force of the surface layer during burnishing was not validated.
OBRABOTKAMETALLOV Vol. 24 No. 1 2022 TECHNOLOGY The purpose of this work is to study the effect of the normal force during dry diamond burnishing with a spherical indenter on smoothing of turned surface microprofi le and on deformation hardening of the 03Cr16Ni15Mo3Ti1 austenitic steel surface layer. Research methodology The study of dry surface burnishing was performed on austenitic stainless steel 03Cr16Ni15Mo3Ti1 (C – 0.03 %; Cr – 16.64 %; Ni – 14.96 %; Mo – 2.77 %; Ti – 1.25 %; Si – 0.53 %; Mn – 0.38 %; Cu – 0.11 %; P – 0.03 %; S – 0.02 %; the rest – Fe). The experimental samples of the “disk” type with a diameter of 104 mm and a thickness of 19 mm were subjected to heat treatment – quenching from the temperature of 1,100 °C (exposure time of 1 hour) with cooling in water. After quenching at the Takisawa EX-310 turning and milling center, the fi nish turning of the sample end surface was performed with a WNMG080408 tool plate using a lubricating and cooling water-emulsion process medium (LCPM) at a cutting speed of 150 m/ min, a feed of 0.08 mm/rev and a cutting depth of 0.3 mm. After turning, the average surface roughness was Ra = 1.0 μm, and the microhardness was 311±10 HV 0.05 and 331±9 HV 0.2. Further, after turning, concentric ring sections with a width of 5 mm were burnished on the treated sample surface (Fig. 1). Burnishing was carried out with a tool able to adjust the burnishing force and to use a spherical indenter with a radius of 2 mm made of natural diamond without using LCPM (in air). The burnishing force varied according to the data of Table. The range of force variation from 100 to 200 N was selected in accordance with the study of burnishing AISI 316Ti analog steel, which was made by Maximov et al. [24]. In accordance with this study, the feed value fb = 0.025 mm/rev was taken. The choice of the indenter sliding speed (vs = 10 m/min) is justifi ed by the maximum permissible speed of dry burnishing the stainless high-chromium steel surface found in [25]. Exceeding the permissible sliding speed leads to a signifi cant increase in roughness and surface layer micro-fractures occurrence. a b Fig. 1. Burnishing of the sample surface on the turning-milling center (a) and annular sections (b), indicated by numbers according to the given burnishing force given in Table Parameters of dry diamond burnishing of ring sections Mode Burnishing force Fb, N Sliding speed vs m/min Feed rate fb, mm/rev 1 200 10 0.025 2 175 3 150 4 125 5 100
OBRABOTKAMETALLOV TECHNOLOGY Vol. 24 No. 1 2022 The surface roughness was studied by 3D profi lometry with a WYKO NT-1100 device. 3D profi lograms were obtained and the average values of the parameter Ra (the arithmetic mean deviation of the profi le) were determined according to the analysis of three surface areas with dimensions of 0.9×1.2 mm and 42.5×55.8 μm. Based on the 3D profi lometry results, the surface microprofi le smoothing coeffi cient was calculated based on the approach proposed in [26]: 100 % t b Ra t Ra Ra Ra (1) where Rat – is the surface roughness after previous (turning) processing; Rab – is the surface roughness after diamond burnishing. Themeasurement of the surfacemicrohardness was performedwith the AHOTECHEcoHARDXM1270C microhardness tester at loads of 0.49 N (50 gf) and 1.96 N (200 gf) on the Vickers indenter. Using the results of surface micro-durometry, the hardening coeffi cient was calculated based on the dependence: HV HV HV 100 %, HV b t t (2) where HVb is the microhardness after surface diamond burnishing; HVt is the initial microhardness of the turned surface. The change in microhardness in the surface layer depth was determined with a cross-section using a SHIMADZU HMV-G21DT microhardness tester under load on a Vickers indenter of 0.245 N (25 gf). Using the Tescan VEGA II XMU scanning electron microscope, the samples surface and the structure of the near-surface layers in cross-sections were studied. Results and discussion In Fig. 2 and Fig. 3a, the results of optical 3D profi lometry of the sample surface after turning and dry diamond burnishing in the zones of 0.9×1.2 mm in size are presented. It can be seen that diamond burnishing led to a signifi cant smoothing of the initial surface roughness and a corresponding decrease in the value of the arithmetic mean deviation of the Ra profi le. As the burnishing force increased from 100 to 150 N, the average value of the roughness parameter Ra decreased from 0.21 to 0.10 μm. A further increase in the burnishing force to 175 and 200 N, on the contrary, caused an increase in the average value of Ra to 0.11 and 0.17 μm, respectively (see Fig. 3a). Calculation by formula (1) showed (Fig. 3b) that in the process of diamond burnishing of an austenitic steel disc in the range of the forces under study, the smoothing coeffi cient δRa ranges from 79 to 90 % with a maximum in the case of using a load Fb = 150 N. Thus, according to the criterion of the profi le arithmetic mean deviation, the specifi ed most favorable normal load mode provides smoothing of the microprofi le by 90 % formed by fi nishing turning (Ra = 1.0 μm), and results in nanoroughness (Ra = 100 nm) even on relatively extended surface areas with dimensions of 0.9×1.2 mm. The surfacemicroprofi le analysis taken in the process of 3Dprofi lometry at microsections with dimension 42.5×55.8 μm showed that, in contrast to the surface after turning with characteristic unidirectional large protrusions and depressions (Fig. 4a), isolated depressions are observed on the entire area of the burnished surface (Fig. 4b-d). With burnishing force of 100 N, these depressions take a shape elongated in the direction of tool movement (Fig. 4b). As burnishing force increases, the size of depressions decreases signifi cantly, it acquires a rounded or oval shape; its distribution becomes more uniform, and the number of depressions increases (Fig. 4c, d).At the same time, the depression depth seems to decrease with an increase in burnishing force, as evidenced by a continuous decrease in the values of the roughness parameter Ra (see Fig. 4 b-d). The presence of the revealed depressions on the burnished surfaces may be due to the insuffi cient amount of the burnishing force and the surface profi le depressions left from the previous turning (Fig. 5a). In particular, this reason can justify the presence of elongated extended depressions on the surface burnished with a minimum investigated force of 100 N (see Fig. 4b). On the other hand, an increase in the number of
OBRABOTKAMETALLOV Vol. 24 No. 1 2022 TECHNOLOGY Fig. 2. Three-dimensional profi lograms on a 0.9 × 1.2 mm area of the disk surface made of 03Cr16Ni15Mo3Ti1 steel, after fi nishing turning (a) and dry diamond burnishing with different forces Fb: 100 N (b), 150 N (c) and 200 N (d) a b c d a b Fig. 3. Dependence of the average values of the roughness parameter Ra (a) and the smoothing coeffi cient δRa (b) of the 03Cr16Ni15Mo3Ti1 steel surface on the burnishing force Fb depressions (indentation) during burnishing with increased loads may result from damage to the austenitic steel surface during its adhesive interaction with a diamond indenter without applying coolant lubricant. Microdurometry of the burnished surface, performed at loads of 0.49 N and 1.96 N with the Vickers indenter, showed a signifi cant effect of the smoothing force on the hardening of the surface layer
OBRABOTKAMETALLOV TECHNOLOGY Vol. 24 No. 1 2022 Fig. 4. Three-dimensional profi lograms taken in a 42.5×55.8 μm area of the disk surface made of 03Cr16Ni15Mo3Ti1 steel, after processing by fi nish turning (a) and dry diamond burnishing with different forces Fb: 100 N (b), 150 N (c), 200 N (d) a b c d a b Fig. 5. SEM images of the surface of a disk made of steel 03Cr16Ni15Мo3Тi1 after processing by fi nishing turning (a) and dry diamond burnishing with a force Fb = 175 N (b)
OBRABOTKAMETALLOV Vol. 24 No. 1 2022 TECHNOLOGY material (Fig. 6). When measuring with a load of 0.49 N, as the burnishing force increases from 100 to 175 N, a non-monotonic increase in microhardness occurs from 409±17 HV 0.05 to 444±7 HV 0.05 (see Fig. 6a). The established maximum level of steel surface microhardness after burnishing with a load of 175 N is observed despite individual micro-destructions in the form of buildups and microcracks as a result of metal redeformation under burnishing effect (Fig. 5b). a b Fig. 6. Dependences of microhardness HV (a) and the hardening coeffi cient δHV (b) of the 03Cr16Ni15Mo3Ti1 steel surface on the burnishing force Fb: microhardness measurements at loads on the Vickers indenter 0.49 N (curves 1) and 1.96 N (curves 2) With a further increase in the burnishing force to 200 N, a decrease in the microhardness of the deformed surface to 422 ± 3 HV 0.05 is observed (Fig. 6a). This can be explained by an occurrence, at the maximum burnishing force, of an over-peening effect, which leads to accumulation of surface damage and local destruction of the thin steel surface layer. This statement is supported by occurrence of noticeable irregularities on the 3D profi logram of the smoothed surface (see Fig. 2d) and a corresponding abrupt increase in roughness after a burnishing force increase from 175 to 200 N (see Fig. 3a). From the data of Fig. 6a it also follows that at measurements using a higher load on the Vickers indenter (of 1.96 N) with increasing the burnishing force, the microhardness of the work surface increases monotonically from 382±4 HV 0.2 after burnishing with a force of 100 N and achieves maximum 421±4 HV 0.2 after burnishing with a force of 200 N. Consequently, the microhardness reduction HV 0.05, associated with the re-peening when increasing burnishing force from 175 to 200 N, affects only a very thin nearsurface layer. Figure 6b shows the effect of the burnishing force on the hardening coeffi cient δHV calculated by formula (2) when burnishing with respect to the microhardness of the initial (after turning) surface of the steel under study. A lower level of initial microhardness (310 ± 10 HV 0.05), found when measuring a thinner layer with a load of 0.49 N than when using a load of 1.96 N (330±9 HV 0.2), indicates damage accumulation directly on the steel surface during the fi nish turning process, causing some material softening. According to Fig. 6b diamond burnishing provided 31...43 % hardening in a thin near-surface layer with an extremum at a burnishing force of 175 N and 15...27 % hardening in a thicker surface layer with a maximum microhardness at a burnishing force of 200 N. Fig. 7 shows microhardness distribution in depth of the gradient-hardened steel surface layer after burnishing at a load of 175 N, which provided a maximum microhardness of 444±7 HV 0.05 of the burnished surface. While moving away from the burnishing surface, the microhardness measured at a load of 0.245 N decreases from 400...420 HV 0.025 to 220...250 HV 0.025 at a depth of 300...350 μm. The study of cross-sections with a scanning electron microscope showed that after fi nishing turning, the large austenitic grain structure is preserved in the sample surface layer (Fig. 8a). Since the technological turning (lathe machining) is designed for sizing cut, accelerated removal of the material cuttings does not create favorable conditions to accumulate large degrees of plastic deformation and structure dispersion accompanying this process in the workpiece surface layer.
OBRABOTKAMETALLOV TECHNOLOGY Vol. 24 No. 1 2022 Fig. 7. Change in the microhardness HV 0.025 in depth of the 03Cr16Ni15Mo3Ti1 steel surface layer (h is the distance from the surface) after dry diamond burnishing with a force Fb = 175 N In contrast to turning, dry diamond burnishing with a force of 175 N formed a pronounced surface layer with a thickness of 30...40 μm with a strongly deformed highly dispersed structure (the layer is marked with a dotted line in Fig. 8b). It can be seen that the deformation led not only to signifi cant austenitic structure dispersion, but also to occurrence of discontinuities in the form of micropores of various sizes – from fractions of a micrometer up to 5 μm (Fig. 8b). Similar micropores were formed in a thin surface layer of AISI 321 metastable austenitic steel as a result of friction treatment with a synthetic diamond indenter in an argon medium [27, 28]. It is known that micropores of deformation origin (submicropores) in plastic metallic materials are formed in the process of submicrocrack blunting that appear in deformable metal when moving dislocations are blocked by barriers such as inclusions, grain boundaries, sliding lines, etc. [29, 30]. Micropores occur as well due to the fact that during the passage of the sliding indenter and its individual microasperity, the metal moves from the zone of compressive stresses, in which deformation occurs in the shear conditions under pressure, into the zone of external tensile stresses [31, 32]. According to [33], the pores in metals under intense plastic deformation are formed precisely in the tension zones, while highly dispersed structures occur only in the zones of shear (compression). Tensile stresses also cause microcracking on the steel surface during burnishing (see Fig. 5b). It is important to note that the highly dispersed layer dotted in Fig. 8b is characterized by a maximum microhardness level of 400...420 HV 0.025 (see Fig. 7). Thus, during microdurometric measurements with loads of 0.245, 0.49 and 1.96 N on the Vickers indenter after dry burnishing with a natural diamond indenter with a force of 175 N, a microhardness level of 400...444 HV was registered on the surface of 03Cr16Ni15Mo3Ti1 austenitic steel and in a surface layer with a thickness of 40 μm. (see Fig. 6a; 7). a b Fig. 8. The structure of the 03Cr16Ni15Mo3Ti1 steel surface layer after fi nish turning (a) and dry diamond burnishing with the force of Fb = 175 N (b); cross-section, scanning electron microscopy, the dotted line indicates the layer boundary with dispersed structure
OBRABOTKAMETALLOV Vol. 24 No. 1 2022 TECHNOLOGY A similar level of deformation hardening (up to 4.1...4.4 GPa) was observed as a result of intensive plastic chromium-nickel austenitic steel deformation by ultrasonic impact treatment with strikers [34], ultrasonic peening in vacuum [35] and equal-channel angular pressing (extrusion) [36]. When processing a workpiece made of AISI 304 metastable austenitic steel by fi nishing turning and diamond burnishing with lubricating fl uid on a turning and milling center, hardening on the surface and surface layer with a thickness of 75 μm to 380...450 HV 0.025 was achieved [23]. Nanostructuring surface machining SMAT of 316L (02Cr17Ni12Mo2Mn2) austenitic steel, similar in composition to 03Cr16Ni15Mo3Ti1 steel studied in this work, led to surface hardening up to 4.5 GPa [37, 38] and surface layer nanostructuring with a thickness of 40 μm with formation of 15 % nanocrystalline strain-induced martensite. In our earlier study [13], on the surface of 03Cr16Ni14Mo3Ti1 austenitic steel under the conditions of friction treatment with a sliding indenter made of synthetic diamond in a nonoxidizing argon medium, an increase in microhardness up to 720 HV 0.025 was observed with a total depth of a gradient-hardened layer of 300 μm. A high coeffi cient of friction (f = 0.47) in the process of friction treatment with a synthetic diamond indenter [13] contributed to more intensive steel hardening than in this work, while when burnishing with a natural diamond indenter, even without lubricating fl uid, the coeffi cient of friction does not exceed 0.1 [39]. In contrast to the works [37, 38], the study [13] observed an almost complete absence of deformation γ→α transformation: in a surface layer ~7 μm thick, no more than 1.5% (vol.) of strain-induced α’-martensite was formed during friction treatment of 03Cr16Ni14Mo3Ti1 steel. The noted result is due to the increased content of nickel (a strong austenite stabilizer) in 03Cr16Ni14Mo3Ti1 steel compared with its amount in 316L (02Cr17Ni12Mo2Mn2) steel [37, 38]. At the same time, in [13], as a result of friction treatment, nano- and submicrocrystalline austenitic structures were formed on the surface of 03Cr16Ni14Mo3Ti1 steel, the occurrence of which was preceded by generation of dislocation cell and band structures. The formation in stable-to-deformation and metastable austenitic steels under frictional impact of highly disordered crystals of nano- and submicrometer dimensions [13-15, 40] occurs at the fi nal stage of structure transformation due to cell turns and its decrement as a result of the development of a rotational deformation mechanism due to friction [41]. Thus, the established increase in microhardness of stable-to-deformation 03Cr16Ni15Mo3Ti1 austenitic steel to 400…444 HV as a result of dry burnishing with an indenter made of natural diamond can be explained by formation of highly dispersed austenite in the surface layer and by corresponding activation of grain boundary and dislocation mechanisms of hardening. Conclusions As a result of the experimental study of the normal force magnitude effect during dry burnishing by a spherical indenter with a radius of 2 mm made of natural diamond at a sliding speed of 10 m/min and a feed value of 0.025 mm/rev on the surface roughness formation and surface layer hardening of stable-todeformation 03Cr16Ni15Mo3Ti1 austenitic steel, it is established: 1) in the studied variation range of the normal burnishing force of 100...200 N, the smoothing coeffi cient of the steel surface initial microprofi le after fi nish turning is 79...90 %, the greatest smoothing with a decrease in the average roughness parameter Ra from 1.0 to 0.1 μm is achieved at a force of 150 N; 2) with diamond burnishing, the initial (after turning) surface is strengthened by 15...43 % (up to 382...444 HV), as the burnishing force increases from 100 to 175 N, a non-monotonic increase in the average microhardness occurs from 409 to 444 HV 0.05 3) burnishing with a load of 175 N forms a gradient-hardened layer with a thickness of 300...350 μm with generated individual micro-fractures on the surface in the form of buildups and microcracks, the maximum hardening of the steel surface is due to formation of a highly dispersed surface layer with a thickness of 30...40 μm with a structure of highly dispersed austenite and corresponding activation of grain boundary and dislocation mechanisms of hardening.
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