Microstructure and mechanical properties of a Ti/TiB metal-matrix composites after multiaxial forging at 850°C to the true strain " = 5:2 were studied. The composite with 17 vol.% of TiB was produced via spark plasma sintering at 1000°

Klimova, M.

Ozerov, M.

Stepanov, N.

Zherebtsov, S.

English

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Vol. 134 (2018) ACTA PHYSICA POLONICA A No. 3Proceedings of the International Symposium on Physics of Materials (ISPMA 14), September 10–15, 2017, PragueStructure and Properties of Ti/TiB Metal–Matrix Compositeafter Isothermal Multiaxial ForgingS. Zherebtsov∗, M. Ozerov, N. Stepanov and M. KlimovaBelgorod State University, Pobeda-85, Belgorod 308015, RussiaMicrostructure and mechanical properties of a Ti/TiB metal–matrix composites after multiaxial forging at850 ◦C to the true strain ε = 5.2 were studied. The composite with 17 vol.% of TiB was produced via sparkplasma sintering at 1000 ◦C. Mechanical behavior in terms of aggregated σ-Σε curves during the multiaxial forgingdemonstrated a pronounced softening following by a steady-like flow stage. The length of TiB whiskers considerablydecreased after the first step of the multiaxial forging and then changed insignificantly. The microstructure afterthe MAF consisted of dislocation-free Ti matrix areas of ≈ 1 µm in diameter and areas with high density of TiBwhiskers and high dislocation density. The forging resulted in a considerable increase in ductility of the Ti/TiBmetal–matrix composites at room and elevated temperatures without loss in strength.DOI: 10.12693/APhysPolA.134.695PACS/topics: 81.20.Ev, 81.40.Gh, 81.40.Lm, 81.70.Bt1. IntroductionOne of the attractive way to increase strength-relatedproperties (strength, hardness, wear resistance, etc.) intitanium and low-alloyed titanium alloys is associatedwith creating Ti matrix composites with embedded ce-ramic reinforcements by, for example, spark plasma sin-tering (SPS) technology [1–3]. Among various rein-forcements TiB has a close to titanium density, it cre-ates minimal residual stresses and has good crystallo-graphic interface with the Ti matrix [4, 5]. During theSPS the TiB whiskers form as a result of the chemi-cal reaction Ti+TiB2 =Ti+2TiB. However, along withthe increased strength, Ti/TiB metal–matrix compos-ites (MMCs) demonstrate poor low-temperature ductil-ity. Mechanical properties of the MMCs can be improvedby thermo-mechanical treatment, for example multipleisothermal 2D forging (drawing) [6, 7]. In this paper, mi-crostructure and mechanical properties of 17 vol.% TiBreinforced titanium matrix composites produced by SPSat 1000 ◦C was studied after multiaxial forging at 850 ◦Cto ε = 5.2.2. Materials and procedureCommercial Ti and TiB2 powders of ≈ 25 and ≈ 4 µmin diameter, respectively, were used as the raw materials.A mixture of 90 wt% Ti and 10 wt% TiB2 (which yields17 vol.% of TiB during the reaction of Ti + TiB2 → Ti +2TiB [8]) was prepared using a Retsch RS 200 vibratingcup mill for 1 h in ethanol at the milling rotation speedof 700 rpm.Ti/TiB MMC specimens measuring 15 mm in heightand 19 mm in diameter were produced using the SPSprocess under vacuum on a Thermal Technology SPS 10-3 machine at 1000 ◦C and 40 MPa for 15 min.∗corresponding author; e-mail: ser_z@mail.ruThe specimens were subjected to multiaxial forging(MAF) which comprised successive compressions of asample along three orthogonal directions (this method isalso known as “abc” deformation [9]). The initial strainrate and the true strain per deformation step were 10−3/sand ≈ 0.5, respectively. Compressions were performedon an Instron 300LX testing machine in air at 850 ◦C.Stress–strain curves were recorded for each step. Tencompressions in total were made (the true cumulativestrain Σε ≈ 5.2).A JEOL JEM-2100 transmission electron microscope(TEM) and a Quanta 600 FEG (field-emission-gun)scanning-electron microscope (SEM) were used for mi-crostructure examination of the central region of thespecimens. SEM specimens were etched using Kroll’sreagent (95% H2O, 3% HNO3, 2% HF)Tensile or compression tests were conducted on an In-stron 5882 testing machine at 300 ◦C, 400 ◦C, and 500 ◦C(tensile) or room temperature (compression) at an ini-tial strain rate of 10−3/s. The tensile samples had thegauge measuring 4 mm length and 3 mm×1.5 mm cross-section. The compression specimens were measured as6 × 4 × 4 mm3. Both the compression and tensile testswere carried out without extensometer mainly due to avery small gage size of the specimens.3. Results and discussionIn the initial (as-sintered) condition the microstruc-ture of the MMC consisted of TiB whiskers with theaverage diameter 63±35 nm heterogeneously distributedwithin the Ti matrix (Fig. 1). In the majority of the mi-crostructure a very high dislocation density was observedmost probably due to a large number of TiB particles.Some unreacted TiB2 particles (the volume fraction of2%) were observed in the microstructure. The residualporosity was ≈ 0.5%.True stress–true strain curves obtained during multi-axial isothermal forging at 850 ◦C showed an initial hard-(695)696 S. Zherebtsov, M. Ozerov, N. Stepanov, M. KlimovaFig. 1. Bright-field TEM image of Ti/TiB MMC mi-crostructure; the inset shows a cross-section of a TiBwhisker.Fig. 2. True stress–true strain curves obtained duringthe MAF at 850 ◦C.ening transient, a peak flow stress, and then flow soften-ing during the first compression (Fig. 2). However at latestages (Σe > 3) each stress–strain curve demonstrated asteady-state-like behavior after initial hardening. A no-ticeable difference between the flow stresses in the end ofeach step and the yield stress of the next step was ob-served. It should be noted also that the flow stress hada trend to decrease with increase of cumulative strain.Microstructure of the Ti/TiB metal–matrix compositechanged considerably as a result of the MAF. A lot ofsmall fragments of TiB were observed in the microstruc-ture of the strained condition (Fig. 3a).Meanwhile TEM analysis showed that deformation at850 ◦C to e = 5.2 (10 steps) resulted in the formationof separate areas (1–1.5 µm in diameter) with a muchlower dislocation density compared with the neighbor-Fig. 3. SEM (a) and TEM bright-field (b) images ofthe Ti/TiB composite after the MAF at 850 ◦C to e =5.2 (10 steps).ing fields (Fig. 3b). The estimated dislocation density inthese areas was ≈ 2×1012 m−2. The boundaries of somedislocation-free areas can be well-defined. The develop-ment of recovery or recrystallization was more evidentin the areas of the Ti matrix with a relatively low den-sity of the TiB whiskers. The greater density of the TiBparticles most likely hindered grain boundary movementthereby preserving the microstructure with a high dislo-cation density.Quantitative analysis showed that the diameter of thewhiskers did not noticeably change during the MAF. Theapparent length of whiskers decreased considerably, by afactor of ≈ 3, after the first step of the MAF and thenremained almost unchanged during further deformation(Fig. 4). Thus, the length-to-diameter aspect ratio of TiBwhiskers approached stable value (≈ 10) at the initialstages of deformation and had not changed further.Structure and Properties of Ti/TiB Metal–Matrix Composite after Isothermal Multiaxial Forging 697Fig. 4. Apparent length of TiB whiskers in Ti/TiBMMCs during the MAF.Mechanical behavior of the MMCs obtained in com-pression at room temperature (Fig. 5a) or in tension at300–500 ◦C (Fig. 5b) showed considerable improvement ofductility of the specimens after the MAF to e = 5.2 (10steps) at 850 ◦C. The samples of the MMC after the MAFat 850 ◦C demonstrated noticeable compression ductility(≈ 2–3%) at room temperature and similar tensile ductil-ity at 300 ◦C. Meanwhile in the as-sintered condition thetensile specimen of MMC fractured just after the elasticregion even at 400 ◦C. Some tensile elongation of the as-sintered composite was recorded only at 500 ◦C. The ulti-mate compression strength of the forged and as-sinteredspecimens was quite similar at room temperature (2210and 1960 MPa, respectively) while at elevated temper-atures the specimens after the MAF became noticeablystronger. Quite a large stage of elasticity observed in allconditions of the MMC can be associated with the con-ducting of the tensile test without extensometer; in thiscase elastic deformation of the tensile machine parts wasalso included into the overall elastic deformation shownin the stress–strain diagram. In addition the Young mod-ulus of the composite is not too high (≈ 200 GPa [4, 10])while the yield stress at room temperature almost at-tained 2000 MPa.After the MAF the ultimate strengths were found to be765 MPa at 300 ◦C and 540 MPa at 400 ◦C while in the as-sintered condition the maximum attained strengths were480 MPa at 400 ◦C and 520 MPa at 500 ◦C.Therefore the results obtained in the current studyshow a possibility to increase considerably low-temperature ductility without loss in strength of theTi/TiB MMCs by the multiaxial isothermal forging at850 ◦C to ε =5.2. The observed improvement of the me-chanical properties is most likely associated with the mi-crostructure developed during the MAF. One of the mostobvious effects of plastic deformation at elevated temper-atures on the microstructure of Ti/TiB MMC was a con-siderable (by ≈ 3 times) decrease in the length of the TiBwhiskers. This change occurred in the very beginning ofFig. 5. Stress–strain curves of Ti/TiB MMC in differ-ent conditions tested in compression at room tempera-ture (a) or in tension at elevated temperatures (b).the MAF (Fig. 4) causing, most likely, the correspond-ing decrease in the flow stress after the first compression(Fig. 2). Since the apparent length of the TiB whiskersdid not decrease noticeably with further strain, a stableaspect ratio of ≈ 10 was achieved. The aspect ratio ofthe TiB (rather than the diameter) is considered to bethe main factor that influences the mechanical propertiesof the MMCs. It was shown in [11] that whiskers with alarge value of aspect ratio make a greater contribution tothe strength of the composite. In turn this can be associ-ated with different contribution of various strengtheningmechanisms (mainly the Orowan mechanism or harden-ing due to a load transfer from the Ti matrix to TiB byan interfacial shear stress [12]) depending on the length-to-diameter ratio. Therefore a stable length-to-diameterratio after the MAF can result in the observed improve-ment of strength and ductility in comparison with theas-sintered condition (Fig. 5).Some difference in the mechanical properties of theMMC after the MAF can also be ascribed to the struc-ture of the Ti matrix. The development of discontinuousdynamic recrystallization in the Ti matrix of the MMCcan be proved by the formation of dislocation-free areas698 S. Zherebtsov, M. Ozerov, N. Stepanov, M. Klimova(Fig. 3b) and characteristic type of the aggregated me-chanical behavior with a steady-like flow stage during theMAF at 850 ◦C (Fig. 2) [13] and agrees with the previousdata [3]. It is known that the presence of recrystallizedareas in nanostructured materials enhance their strainhardening capacity and thus promote ductility [14]. Inthe studied Ti/TiB composite, the combination of therecrystallized Ti grains and the areas with high disloca-tion density strengthened by the nanosized TiB whiskersprovides a good balance of strength and ductility whichexceeds the corresponding properties of the as-sinteredmaterial.4. Conclusions1. Mechanical behavior during the MAF at 850 ◦C canbe described by an aggregated σ–Σε curves whichdemonstrated a pronounced softening following bya steady-like state flow. The observed mechanicalbehavior can be associated with the formation ofa stable aspect ratio of ≈ 10 of the TiB whiskersduring the MAF and development of discontinu-ous dynamic recrystallization. The MAF resultedin the formation of a homogeneous microstructurewith dislocation-free areas of ≈ 1 µm and areaswith high density of TiB and high dislocation den-sity.2. The MAF at 850 ◦C to cumulative strain ≈ 5.2 re-sulted in a considerable increase in low-temperatureductility without loss in strength. For instance,nearly zero ductility was obtained in the as-sinteredspecimen during compression at room temperature,whereas specimens after the MAF demonstrated atthis temperature ≈ 3% ductility.AcknowledgmentsThe work was supported by the Russian Science Foun-dation under Grant No. 15-19-00165. The authors arealso grateful to Joint Research Center “Materials andTechnologies”, Belgorod State University, for the assis-tance with instrumental analysis.References[1] T. Saito, T. Furuta, T. Yamaguchi, in: RecentAdvances in Titanium Metal Matrix Composites,Eds. F.H. Froes, J. Storer, The Minerals, Metals andMaterials Society, Warrendale 1995, p. 33.[2] L.J. Huang, L. Geng, H-X. Peng, Prog. Mater. Sci.71, 93 (2015).[3] M. Ozerov, M. Klimova, A. Kolesnikov, N. Stepanov,S. Zherebtsov, Mater. Des. 112, 17 (2016).[4] K. Morsi, V.V. Patel, J. Mater. Sci. 42, 2037 (2007).[5] H. Feng, Y. Zhou, D. Jia, Q. Meng, J. Rao,Cryst. Growth Des. 6, 1626 (2006).[6] R.A. Gaisin, V.M. Imayev, R.M. Imayev, J. AlloysComp. 723, 385 (2017).[7] V. Imayev, R. Gaisin, E. Gaisina, R. Imayev, H.-J. Fecht, F. Pyczak, Mater. Sci. Eng. A Struct. 609,34 (2014).[8] L.J. Huang, L. Geng, B. Wang, L.Z. Wu, Mater. Des.45, 532 (2013).[9] G.A. Salishchev, S.Yu. Mironov, S.V. Zherebtsov,Rev. Adv. Mater. Sci. 11, 152 (2006).[10] K.S. Ravi Chandran, K.B. Panda, S.S. Sahay, JOM56, 42 (2004).[11] M.Y. Koo, J.S. Park, M.K. Park, K.T. Kim,S.H. Hong, Scr. Mater. 66, 487 (2012).[12] B. Chen, J. Shen, X. Ye, L. Jia, S. Li, J. Umeda,M. Takahashi, K. Kondoh, Acta Mater. 140, 317(2017).[13] F. Humphreys, M. Hatherly, Recrystallization and Re-lated Annealing Phenomena, Elsevier, Oxford 2004.[14] Y. Wang, M. Cheng, F. Zhou, E. Ma, Nature 419,912 (2002).

Structure and properties of Ti/TiB metal-matrix composite after isothermal multiaxial forging

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Structure and properties of Ti/TiB metal-matrix composite after isothermal multiaxial forging

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