Vol. 27 No. 3 2025 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. 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 Journal “Obrabotka Metallov – Metal Working and Material Science” is indexed in the world's largest abstracting bibliographic and scientometric databases Web of Science and Scopus. 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.
OBRABOTKAMETALLOV Vol. 27 No. 3 2025 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 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. Korotkov, D.Sc. (Engineering), Professor, Kuzbass State Technical University, Kemerovo; 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, V.P. Larionov Institute of the Physical-Technical Problems of the North of the Siberian Branch of the RAS, Yakutsk; Alexander S. Yanyushkin, D.Sc. (Engineering), Professor, I.N. Ulianov Chuvash State University, Cheboksary
Vol. 27 No. 3 2025 5 CONTENTS OBRABOTKAMETALLOV TECHNOLOGY Kondratiev V.V., Gozbenko V.E., Kononenko R.V., Konstantinova M.V., Guseva E.A. Determination of the main parameters of resistance spot welding of Al-5 Mg aluminum alloy..................................................................................... 6 Gvindjiliya V.E., Fominov E.V., Marchenko A.A., Lavrenova T.V., Debeeva S.A. Infl uence of cutting speed on pulse changes in the temperature of the front cutter surface during turning of heat-resistant steel 0.17 C-Cr-Ni-0.6 Mo-V................................................................................................................................................................ 23 Karelin R.D., Komarov V.S., Cherkasov V.V., OsokinA.A., Sergienko K.V., Yusupov V.S., Andreev V.A. Production of rods and sheets from TiNiHf alloy with high-temperature shape memory eff ect by longitudinal rolling and rotary forging methods.................................................................................................................................................................... 37 EQUIPMENT. INSTRUMENTS Zakovorotny V.L., Gvindjiliya V.E., Kislov K.V. Information properties of vibroacoustic emission in diagnostic systems for cutting tool wear................................................................................................................................................ 50 Zhukov A.S., Ardashev D.V., Batuev V.V., Kulygin V.L., Schuleshko E.I. Modal analysis of various grinding wheel types for the evaluation of their integral elastic parameters...................................................................................... 71 Nishandar S.V., Pise A.T., Bagade P.M. Numerical and experimental investigation of heat transfer augmentation in roughened pipes................................................................................................................................................................ 87 Nosenko V.A., Rivas Perez D.E., Alexandrov A.A., Sarazov A.V. The eff ect of the grinding method on the grain shape coeffi cient of black silicon carbide....................................................................................................................................... 108 MATERIAL SCIENCE Karlina Yu.I., Konyukhov V.Yu., Oparina T.A. Investigation of the process of surface decarburization of steel 20 after cementation and heat treatment.................................................................................................................................. 122 Kovalevskaya Z.G., Liu Y. Eff ect of heat treatment on the structure and properties of high-entropy alloy AlCoCrFeNiNb0.25............................................................................................................................................................. 137 Sirota V.V., Prokhorenkov D.S., Churikov A.S., Podgorny D.S., Alfi mova N.I., Konnov A.V. Corrosion properties of coatings produced from self-fl uxing powders by the detonation spraying method............................................................ 151 Filippov A.V., Shamarin N.N., Tarasov S.Yu., Semenchyuk N.A. The infl uence of structural state on the mechanical and tribological properties of Cu-Al-Si-Mn bronze............................................................................................................. 166 Waheed F., Qayoom A., Shirazi M.F. Fabrication, characterization and performance evaluation of zinc oxide doped nanographite material as a humidity sensor......................................................................................................................... 183 Dolgova S.V., Malikov A.G., Golyshev A.A., Nikulina A.A. Features of the structure of gradient layers «steel - Inconel - steel», obtained by laser direct metal deposition.................................................................................................. 205 Burkov A.A., Dvornik M.A., Kulik M.A., Bytsura A.Yu. The infl uence of tungsten carbide particle size on the characteristics of metalloceramic WC/Fe-Ni-Al coatings.................................................................................................... 221 Patil S., Chinchanikar S. Investigation on the mechanical properties of stir-cast Al7075-T6-based nanocomposites with microstructural and fractographic surface analysis...................................................................................................... 236 EDITORIALMATERIALS 252 FOUNDERS MATERIALS 263 CONTENTS
OBRABOTKAMETALLOV Vol. 27 No. 3 2025 technology Production of rods and sheets from TiNiHf alloy with high-temperature shape memory effect by longitudinal rolling and rotary forging methods Roman Karelin a, *, Viktor Komarov b, Vladimir Cherkasov c, Artem Osokin d, Konstantin Sergienko e, Vladimir Yusupov f, Vladimir Andreev g A.A. Baykov Institute of Metallurgy and Materials Science of the Russian Academy of Sciences, 49 Leninsky Ave., Moscow, 119334, Russian Federation a https://orcid.org/0000-0002-4795-8668, rdkarelin@gmail.com; b https://orcid.org/0000-0003-4710-3739, vickomarov@gmail.com; c https://orcid.org/0000-0002-5450-3565, cherkasov.vv@misis.ru; d https://orcid.org/0009-0008-4945-3648, art.osokin1201@icloud.com; e https://orcid.org/0000-0003-4018-4599, shulf@yandex.ru; f https://orcid.org/0000-0002-0640-2217, vsyusupov@mail.ru; g https://orcid.org/0000-0003-3937-1952, andreev.icmateks@gmail.com Obrabotka metallov - Metal Working and Material Science Journal homepage: http://journals.nstu.ru/obrabotka_metallov Obrabotka metallov (tekhnologiya, oborudovanie, instrumenty) = Metal Working and Material Science. 2025 vol. 27 no. 3 pp. 37–49 ISSN: 1994-6309 (print) / 2541-819X (online) DOI: 10.17212/1994-6309-2025-27.3-37-49 ART I CLE I NFO Article history: Received: 07 July 2025 Revised: 28 July 2025 Accepted: 07 August 2025 Available online: 15 September 2025 Keywords: Shape memory alloy Rolling Hardness Rotary forging Funding The study was conducted with the financial support of the State Task of IMET RAS on 2025 year № 07500319-25-00. ABSTRACT Introduction. Ti-Ni based shape memory alloys (SMAs) are functional materials that find widespread practical application in engineering and medicine. Functional properties of Ti-Ni based alloys are sensitive to the chemical composition. To develop alloys with specific properties, ternary SMAs are being actively developed. For example, TiNiHf ternary alloys are characterized by a high-temperature shape memory effect. Today, there is a demand for SMAs used in the production of functional elements with a response temperature of more than 120 °C. These alloys must also have sufficient ductility to obtain deformed semi-finished products for the subsequent manufacture of heat-sensitive functional elements. Also among the current issues of developing the practical application of TiNiHf alloys is the lack of technological schemes for obtaining semi-finished products from TiNiHf SMAs. The purpose of this work is study the feasibility of conducting deformation processing of the studied TiNiHf alloys with a hightemperature shape memory effect and to identify the relationships between phase composition and mechanical characteristics and the applied processing method. In this work, the possibility of producing sheets and rods from TiNiHf alloys with 5 and 10 at.% Hf and 50.0 at.% Ni by longitudinal rolling, caliber rolling, and rotary forging was investigated. The research methods were: X-ray analysis, differential scanning calorimetry, and measurement of Vickers hardness. Results and discussion. It was found that the TiNiHf alloy with 10 at.% Hf has insufficient ductility. From the alloy with 5 at.% Hf, blanks in the form of sheets and rods of various sizes were obtained by using longitudinal rolling and rotary forging processes. It was shown that hot deformation allows increasing the hardness of the studied TiNiHf alloy with 5 at.% Hf compared to the cast state, from 232 HV to 242–264 HV. Cold deformation leads to a significant increase in hardness values up to 362–394 HV. Characteristic temperatures of the forward and reverse martensitic transformation are quite stable. The obtained results indicate the potential of using longitudinal rolling and rotary forging to obtain semi-finished products of TiNiHf alloys with 5 at.% Hf and to improve the functional and mechanical properties of the alloy after smelting. For citation: Karelin R.D., Komarov V.S., Cherkasov V.V., Osokin A.A., Sergienko K.V., Yusupov V.S., Andreev V.A. Production of rods and sheets from TiNiHf alloy with high-temperature shape memory effect by longitudinal rolling and rotary forging methods. Obrabotka metallov (tekhnologiya, oborudovanie, instrumenty) = Metal Working and Material Science, 2025, vol. 27, no. 3, pp. 37–49. DOI: 10.17212/1994-63092025-27.3-37-49. (In Russian). ______ * Corresponding author Karelin Roman D., Ph.D. (Engineering), A.A. Baykov Institute of Metallurgy and Materials Science of the Russian Academy of Sciences, 49 Leninsky ave., 119334, Moscow, Russian Federation Tel.: +7 916 590-42-76, e-mail: rdkarelin@gmail.com Introduction Shape memory alloys (SMAs) based on titanium nickelide are functional materials that receive widespread practical application in engineering and medicine due to their unique shape memory properties, high mechanical characteristics, corrosion resistance, and biocompatibility [1–7]. In order to regulate their
OBRABOTKAMETALLOV technology Vol. 27 No. 3 2025 functional behavior and obtain materials with special properties, the use of ternary titanium nickelide alloys containing Cu, Fe, Co, Nb, and Hf is being actively developed [8-11]. Among these alloys for high-temperature applications, alloys of the TiNiHf system should be highlighted [12–14]. Most scientific research in this field focuses on alloys with 20 at.% Hf and 50.3 at.% Ni, which provide a temperature range of shape recovery (TRSR) of 200–350 °C [15–19]. The high Hf (20 at.%) and Ni (over 50 at.%) content is attributed to observations from previous studies, which suggest that TiNiHf alloys become brittle and difficult to deform when the combined concentration of Ti and Hf exceeds 49.8 at.%. Embrittlement is attributed to the precipitation of a significant amount of an embrittling (Ti, Hf)2Ni-type phase [20]. To mitigate this, the nickel concentration is typically increased. However, if other elemental contents remain unchanged, the martensitic transformation temperature range will decrease accordingly. Therefore, a higher Hf concentration is required to achieve a high-temperature shape memory effect in these alloys. However, high Hf content significantly increases the cost, hindering their practical application. Moreover, the application of TiNiHf SMAs is also challenged by the limited control over martensitic transformation temperatures. Several industries currently require shape-memory alloys with a TRSR ranging from 120 to 200 °C, coupled with sufficient technological plasticity for the production of thermosensitive components. In addition, a significant challenge in expanding the practical applications of TiNiHf alloys lies in developing the technology for manufacturing semi-finished products of various grades, a task inextricably linked to the advancement of novel thermomechanical processing methods [21]. Earlier studies showed that rods with high mechanical properties and a shape recovery temperature of 155 °C after 2% bending could be obtained from the Ti49.0Ni49.5Hf1.5 alloy using rotary forging [22]. Reference [23] also demonstrated that a pulsed electric current could improve the technological plasticity of the Ti47.4Ni47.6Hf5.0 alloy during cold rolling. Based on the preceding discussion, and as part of our effort to develop methods for creating semifinished TiNiHf SMA products with lower Hf and Ni content, the first purpose of this study is to explore the application of thermomechanical treatments to TiNiHf alloys with 5 and 10 at.% Hf and 50 at.% Ni, using different deformation methods. The second purpose is to determine how the phase composition and mechanical characteristics of TiNiHf alloys change depending on the deformation method used. This paper investigates the production of semi-finished sheets and rods using longitudinal rolling, caliber rolling, and rotary forging. The alloy’s structure and mechanical properties were also analyzed using X-ray analysis, differential scanning calorimetry, and Vickers hardness testing. A significant result is the successful production of Ti45.0Ni50.0Hf5.0 alloy semi-finished products, including sheets (2.2 and 1.0 mm thick), a rectangular bars (6.9 × 8.5 mm), and a 5.1 mm diameter rods, all demonstrating high hardness and stable phase composition. Methods The study used two alloys with compositions Ti45.0Ni50.0Hf5.0 and Ti40.0Ni50.0Hf10.0. The starting materials were 99.99% pure iodide titanium, 99.99% pure nickel (H0 grade), and 2.5 mm diameter hafnium wire (GFI-1 grade). TiNiHf ingots containing 5 and 10 at.% Hf were produced by vacuum electric arc melting, with eight remelting cycles, and cast into a water-cooled copper mold. Hot deformation was performed by longitudinal flat and bar rolling on a DUO 300 two-roll rolling mill and by rotary forging at 850 °C. The bar rolling used a square-to-square pass schedule, with the square side changing as follows: 19→17→15→13→11→9→8→7→6 mm. Cold rolling was then performed on a QUARTO110/300 fourroll rolling mill. The martensitic transformation temperature range (TRMT) in the as-cast alloy was studied by differential scanning calorimetry (DSC) using a Mettler Toledo DSC 3+ calorimeter with a heating and cooling rate of 10 °C/min from 0 to 200 °C. The martensitic transformation temperature range (TRMT) was measured using differential scanning calorimetry (DSC) on a Mettler Toledo DSC 3+ calorimeter, with a heating/cooling rate of 10 °C/min from 0 to 200 °C. The phase composition was analyzed by X-ray diffraction analysis (XRD) using a DRON-3
OBRABOTKAMETALLOV Vol. 27 No. 3 2025 technology diffractometer with CuKα radiation at 2θ angles from 35 to 47° [18, 24]. Vickers hardness was measured at room temperature using a LECOM 400-A hardness tester under a 1 N load to determine mechanical properties. Result and Discussion Initial TiNiHf SMA Ingots Fig. 1 shows the general appearance of the ingots produced by electron beam melting. Table 1 presents the mass, dimensions, and chemical composition of the ingots. a b c Fig. 1. Photographs of ingots 1 (a), 2 (b), and 3 (c) of TiNiHf SMA after vacuum arc melting with 8-fold remelting Ta b l e 1 Weight, dimensions and estimated composition of the TiNiHf ingots Ingot No. Weight, g Dimensions, (h × b × L) mm Chemical composition mass % at.% Ti Ni Hf Ti Ni Hf 1 148.84 9.5 × 18.1 × 137.5 28.87 44.23 26.90 40.0 50.0 10.0 2 150.15 10.4 × 18.5 × 136.9 36.03 49.06 14.92 45.0 50.0 5.00 3 149.12 9.8 × 17.8 × 137.5 28.87 44.23 26.90 40.0 50.0 10.0 After melting, the martensitic transformation temperature range (TRMT) of the ingots was analyzed using differential scanning calorimetry (DSC). Characteristic calorimetric curves are shown in Fig. 2. DSC analysis of samples fromingots 1 and 3 showed no peaks for either forward or reverse transformations within the temperature range studied. Ingot 2, however, showed a reverse MT with starting and finishing temperatures of 63 °C and 124 °C, respectively. This wide temperature range is typical for as-cast ingots due to potential internal stresses and segregation. To improve homogeneity, ingot 1 was initially subjected to a 12-hour homogenization annealing at 1,100 °C in vacuum. However, the ingot melted during annealing, possibly due to the formation of phases with lower melting temperatures during cooling after melting. Therefore, it was decided not to
OBRABOTKAMETALLOV technology Vol. 27 No. 3 2025 Fig. 2. Calorimetric curves of ingots 1, 2, and 3 of TiNiHf SMA use homogenization annealing, and ingots 2 and 3 were deformed in the as-cast state. Homogenization annealing was therefore excluded from the production process for TiNiHf SMA semi-finished products to optimize the technology. Production of TiNiHf SMA semi-finished products Before deformation, the ingots were cut into two parts. The resulting ingots had the following dimensions: 2-1 – 10.4 × 18.5 × 53.1 mm and 2-2 – 10.4 × 18.5 × 77.1 mm; 3-1 – 9.8 × 17.8 × 52.1 mm and 3-2 – 9.8 × 17.8 × 76.7 mm. Hot deformation of ingots 2-1 and 3-1 was first performed by longitudinal rolling at 850 °C. The samples were preheated for 15 minutes without a protective atmosphere to improve rolling workability, unlike previous studies [23] where heating was in a protective argon atmosphere, with 3–5 minute reheating before each pass. The relative strain in one pass was kept below 15%. Hot rolling of ingot 2-1 produced a sheet with dimensions 2.2 × 27.5 × 167.9 mm. However, ingot 3-1 fractured after only 2 passes, accumulating a relative strain of 12%. Considering the lack of distinct peaks on the calorimetric curves, the melting of the similar ingot 1 during homogenization annealing, and the alloy’s low workability, it’s likely that ingot 3 contained many undesirable secondary phases formed during cooling after melting or during heating for rolling. This suggests that the alloy with 5 at.% Hf has better workability than the alloy with 10 at.% Hf. Fig. 3 shows photos of the sheet from ingot 2-1 and the fractured ingot 3-1.
OBRABOTKAMETALLOV Vol. 27 No. 3 2025 technology a b Fig. 3. Photographs of the obtained sheet from ingot 2-1 (TiNiHf alloy) with a thickness of 2.2 mm (a) and ingot 3-1 after fracture (b) Further deformation by hot bar rolling (HBR) and rotary forging (RF) was only done on ingot 2-2 of the TiNiHf alloy with 5 at.% Hf. Initially, two passes were rolled in one caliber from a single heating cycle, taking advantage of deformation heating. However, when switching to the second caliber, cracks appeared at the back end of the ingot. This suggests that the alloy has a narrow temperature range for plastic deformation. To prevent the ingot from cooling down, it was reheated after each pass. Changing the rolling pattern and eliminating the second pass without preheating resulted in successful rolling without fracture or new cracks. This produced a rectangular bar measuring 6.9 × 8.5 × 236.4 mm. After bar rolling, a 150 mm long sample was cut from the bar for rotary forging. Rotary forging was carried out at a deformation temperature of 850 °C, with a relative strain per pass below 10%, and the ingot was heated between each pass for 10-15 minutes. This produced a rod with a diameter of 119 mm. It’s worth noting that, unlike the approach in [23], the section of ingot 2 used here was rotary forged after prior deformation rather than in the as-cast state. This highlights the potential for combining hot bar rolling and rotary forging to produce TiNiHf SMA rods. Fig. 4 shows a photo of the bars after rolling and rotary forging. a b Fig. 4. Photograph of a TiNiHf alloy rod after caliber rolling (a) and rotary forging (b) It should be noted that rotary forging had difficulties with rod alignment and chipping at the ends, likely due to cooling. Because of this, further rotary forging to smaller diameters (which would cool even faster) wasn’t attempted. Next, a 2.1 × 27.5 × 56 mm sample was cut from the hot-rolled sheet from ingot 2-1 for cold rolling (CR). After cutting, the sample was cleaned to remove the surface oxide layer by grinding and chemical etching in a mixture of nitric and hydrofluoric acids. The sheet thickness before rolling was 2.1 mm. Cold rolling was carried out with a relative strain per pass below 10%. Prior work found the critical relative strain for cold rolling TiNiHf alloy to be 20% [22]. Therefore, cold rolling was carried out with intermediate annealing at a temperature of 850 °C for 10 minutes upon reaching a relative degree of deformation close to 20%. After cold rolling to 1.04 mm, a sample was cut from the sheet for further cold rolling to fracture to redetermine the critical strain. Fig. 5 shows the sheet before and after cold rolling, thus concluding our description of the cold rolling process.
OBRABOTKAMETALLOV technology Vol. 27 No. 3 2025 Cold rolling the TiNiHf SMA sample to its critical strain showed that fracture (a through-crack at the front end) occurred after a total relative strain of 23%, with a final sample thickness of 0.93 mm. This confirms that intermediate annealing is needed during cold rolling of TiNiHf alloy samples after a total strain of 20%. Next, we studied how the phase composition and mechanical properties of the TiNiHf + 5 at.% Hf alloy changed depending on the processing method. Investigation of the phase state and mechanical properties of TiNiHf SMA samples following application of various deformation methods Fig. 6 shows the Vickers hardness of alloy 2 after deformation using different methods. a b Fig. 5. General view of the TiNiHf SMA sheets before (a) and after (b) cold rolling Fig. 6. Hardness of TiNiHf SMA samples after various deformation methods Hot deformation slightly increased the Vickers hardness compared to the as-cast ingot 2 (232 HV): hardness after HR and HRF was about 242 HV, and after HBR it was 264 HV. This is typical for hightemperature heat treatment and related to dynamic and static recrystallization. Cold deformation to 1 mm thickness greatly increased hardness to 362 HV, with a maximum of 394 HV after CR to the critical strain leading to fracture. This is likely due to the increased crystal lattice defects after CR. The hot deformation results suggest that it occurs at a steady stage with dynamic recrystallization and stress relaxation from deformation hardening, unlike CR, which results in a heavily deformed structure. Fig. 7 shows the X-ray analysis results for alloy 2 after various deformation methods. X-ray analysis showed that martensite was the main phase in alloy 2 samples at room temperature, both before and after deformation. This agrees with the DSC data. The absence of B2-austenite peaks confirms that the reverse MT occurs above room temperature. (Ti, Hf)2Ni phase lines, formed during cooling after
OBRABOTKAMETALLOV Vol. 27 No. 3 2025 technology Fig. 7. X-ray diffraction patterns of TiNiHf SMA samples after the studied processing methods melting, were seen at 2θ angles of 41° and 45°. Hot deformation didn’t significantly broaden the X-ray lines, but cold rolling did. The changes in the sample line profile after cold rolling confirm significant deformation hardening and increased crystal structure defects. Fig. 8 and Table 2 show the martensitic transformation temperature range (TRMT) measured by DSC after the different processing methods on ingot 2. Fig. 2 shows the initial DSC curves of the TiNiHf SMA ingots. Fig. 8. Calorimetric curves of the samples of ingot 2 (TiNiHf SMA) after the studied processing methods: hot rolling (HR) (a), cold rolling (CR) (b), hot rotary forging (HRF) (c), and hot longitudinal rolling (HLRR) (d) a b c d
OBRABOTKAMETALLOV technology Vol. 27 No. 3 2025 Ta b l e 2 Martensitic transformation temperatures of processed TiNiHf SMA (Ingot 2) Sample Direct transformation Reverse transformation Ms, °С Mf, °С Mp, °С As, °С Af, °С Ap, °С Initial 74 50 21 62 92 124 HR 54 40 17 61 85 105 HRF 65 50 31 71 97 115 HBR 62 47 27 70 97 113 CR 54 36 17 52 85 107 The results showthat neither hot nor colddeformation significantly changes themartensitic transformation temperatures; they remain relatively stable with fluctuations under 10 °C. However, there’s a trend of decreasing forward MT (Af) temperature compared to the as-cast state of ingot 2. Even so, this temperature stays above 105 °C in all cases, indicating that the TiNiHf alloy maintains its high-temperature shape memory behavior. Conclusion A comprehensive investigation was undertaken to assess the feasibility of producing a range of semifinished products from TiNiHf shape memory alloys containing 5 and 10 at.% Hf with reduced Ni content, utilizing various deformation methods. Based on the findings of this study, the following conclusions can be drawn: The TiNiHf SMA with 10 at.% Hf lacks sufficient technological plasticity for thermomechanical treatment by the considered deformation methods. The TiNiHf SMA with 5 at.% Hf has sufficient technological plasticity Various deformation methods were applied to the alloy (hot and cold longitudinal rolling, bar rolling, rotary forging). High-quality semifinished products in the form of sheets and rods of various sizes were obtained. Hot deformation increases hardness from 232 HV (as-cast) to 242 HV (HR/HRF) and 264 HV (HBR). Cold deformation significantly increases hardness, reaching 362 HV (1 mm thick sheet) and 394 HV (rolling to critical strain). The characteristic temperatures of the forward and reverse martensitic transformations in the TiNiHf SMA with 5 at.% Hf remain stable after deformation. Deformation slightly decreases the finishing temperature of the reverse martensitic transformation (Af) (to 19 °C) compared to the as-cast ingot. However, Af remains above 105 °C, confirming their high-temperature shape memory behavior. Thermomechanical processing using hot and cold rolling and rotary forging is a promising method for producing TiNiHf SMA semi-finished products with 5 at.% Hf and improving the alloy’s functional and mechanical properties after melting. References 1. Sadashiva M., Sheikh M.Y., Khan N., Kurbet R., Gowda T.D. A review on application of shape memory alloys. International Journal of Recent Technology and Engineering (IJRTE), 2021, vol. 9 (6), pp. 111–120. DOI: 10.35940/ ijrte.F5438.039621. 2. Nair V.S., Nachimuthu R. The role of NiTi shape memory alloys in quality of life improvement through medical advancements: A comprehensive review. Proceedings of the Institution of Mechanical Engineers, Part H: Journal of Engineering in Medicine, 2022, vol. 236 (7), pp. 923–950. DOI: 10.1177/09544119221093460. 3. Kim M.S., Heo J.K., Rodrigue H., Lee H.T., Pané S., Han M.W., Ahn S.H. Shape memory alloy (SMA) actuators: The role of material, form, and scaling effects. Advanced Materials, 2023, vol. 35 (33), p. 2208517. DOI: 10.1002/adma.202208517.
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