Inﬂuence of the Microstructure of the Initial Material on the Zn Wires Prepared by Direct Extrusion with a Huge Extrusion Ratio

: In this study, we prepared zinc wires with a diameter of 250 µ m by direct extrusion using an extrusion ratio of 576. We studied the inﬂuence of the extrusion temperature and microstructure of the initial Zn billets on the microstructural and mechanical characteristics of the extruded wires. The extrusion temperature played a signiﬁcant role in the ﬁnal grain size. The wires extruded at 300 ◦ C possessed a coarse-grained microstructure and the shape of their tensile stress–strain curves suggested that twinning played an important role during their deformation. A signiﬁcant inﬂuence of the initial grain size on the ﬁnal microstructure was observed after the extrusion at 100 ◦ C. The wires prepared from the billet with a very coarse-grained microstructure possessed a bimodal grain size. A signiﬁcant coarsening of their microstructure was observed after the tensile test. The wires prepared from the medium-grained billets at 100 ◦ C were relatively coarse-grained, but their grain size was stable during the straining, resulting in the highest ultimate tensile strength. This preliminary study shows that strong attention should be paid to the extrusion parameters and the microstructure of the initial billets, because they signiﬁcantly inﬂuence the microstructure and mechanical behavior of the obtained wires.


Introduction
Zinc and Zn-based materials have been extensively studied as absorbable materials for medical applications [1][2][3][4][5]. In contrast to the other two metals (Fe and Mg) considered as absorbable materials, zinc and its alloys possess a more appropriate corrosion rate in the body environment [6,7]. Zinc possesses a low melting point (~420 • C) and its casting can be performed in the air, which is a major benefit from an economical point of view.
The main drawback of zinc and its alloys is their poor strength (~30 MPa, pure zinc) and ductility (~0.25%, pure zinc) [7,8] in the as-cast state. Cast zinc is usually coarsegrained; the increasing grain size decreases the critical resolved shear stress (CRSS) for twinning, which is the predominant deformation mechanism in coarse-grained Zn-based materials [9]. The extensive twinning leads to the twin-twin and twin-dislocation interactions, resulting in the formation of cracks and a subsequent decrease in ductility [10,11]. The mechanical performance can be enhanced by appropriate refinement of the microstructure. The medium-grained Zn-based materials deform mainly by dislocation slip, which results in an increase in both strength and ductility [9,12]. Another decrease in the grain-size can lead to a decrease in strength and increase in ductility due to the activation of the creep-like deformation mechanisms (dislocation climb, grain boundary sliding) [9,13]. The

Preparation Process
Pure Zn rods (99.9999 wt.%, Puratronic ® ) were annealed to obtain two different microstructures. The annealing was performed in a Xerion electric resistance furnace (Xerion, Berlin, Germany) in an atmosphere of 99.999% argon gas at 400 • C for 72 h or at 100 • C for 1 h. After the annealing, the materials were cooled in the furnace to ambient temperature.

Microstructure
The microstructure of the annealed rods (initial materials for the extrusion process) was observed using a light metallographic microscope Zeiss Axio Observer D1m (Carl Zeiss Microscopy GmbH, Jena, Germany). For this observation, metallographic cross-sections were prepared by electro-erosive cutting, subsequent grinding on SiC sandpapers and chemical polishing in a solution consisting of 100 mL of distilled water, 5 mL of nitric acid (65 wt.%), 20 g of chromium (VI) oxide and 1.5 g of sodium sulphate. The microstructure was revealed by chemical etching in a mixture containing 1.5 g of sodium sulphate, 20 g of chromium (VI) oxide and 100 mL of distilled water.
The microstructure of the annealed rods will be shown and described in the Results section. The materials significantly differed in their grain size; therefore, they will be called coarse-grained (annealed at 400 • C) and medium-grained (annealed at 100 • C) Zn.

Extruded Wires 2.2.1. Preparation Process
From the annealed rods, cylinders with a diameter of 5.95 mm and length of 20 mm were machined and extruded using a steel in-house-made extrusion mold with an extrusion ratio of 576. This extrusion ratio corresponds to the imposed true strain of 6.36.
The imposed true strain can be calculated according to Equation (1) [24]: where ε imp is the imposed true strain and ER is the extrusion ratio (576). The extrusion was performed at two different temperatures, namely 100 • C and 300 • C. The extrusion mold was heated to the desired extrusion temperature using electricresistance elements. The extruded billets and the mold were carefully lubricated using a MoS 2 high-temperature paste. The billets were placed into the extrusion mold (diameter of the billet container 6 mm) and tempered at the extrusion temperature for 10 min. Subsequently, the billets were passed through the channel with a diameter of 250 µm using an in-house-built hydraulic press. The ram speed of 0.2 mm/s was used. After the extrusion, the wires were wound up a spool with a diameter of 100 mm. The designation of the Zn wires prepared from the initial materials with a different microstructure and at various extrusion temperatures is listed in Table 1. The designation mentioned in Table 1 will be used further in the text to enhance its lucidity, especially to abbreviate the labels and captions in figures and plots. The surface of the wires was chemically polished in the same etching solution as was used for the initial material (Section 2.1.2). Subsequently, the microstructure was highlighted by chemical etching in a mixture containing 1.5 g of sodium sulphate, 20 g of chromium (VI) oxide and 100 mL of distilled water. After both chemical polishing and etching, the wires were rinsed with distilled water and ethanol.
The surfaces of the wires were documented using a FEI Phenom scanning electron microscope (SEM, ThermoFisher Scientific, Pfeddersheim, Germany). The average grain size was evaluated by the image analyses of the SEM micrographs of the etched wire surfaces. The ImageJ software (v.1.53e, Wayne Rasband and National Institutes of Health, MD, USA) was used for this purpose.
The cross-and longitudinal sections of the as-extruded wires and the cross-sections of the wires after mechanical testing were prepared by focused ion beam milling (FIB). The FIB milling was performed by a fully integrated Xe plasma source FIB using a scanning electron microscope (FIB-SEM) TESCAN FERA3 GM (TESCAN, Brno, Czech Republic). The process was monitored by secondary electron (SE) imaging (Everhart-Thornley SE detector) at 5 kV/120-260 pA. For both cross-and longitudinal section FIB milling of the Zn wires, FIB conditions of 30 kV/1 µA were used for the initial rough milling of the material, followed by more precise polishing at 30 kV/300 nA, which was a sufficient surface treatment for observing electron backscattered diffraction (EBSD) patterns.
EBSD analyses were performed in the same FIB-SEM system using a versatile EDAX DigiView 5 high-resolution digital camera and electron beam at conditions of 30 kV/4.86 nA with a 70 • sample pre-tilted stub holder at a working distance WD = 14 mm. The MG Zn wires were analyzed with a 0.40 µm step for both cross-and longitudinal section mapping, whereas the CG wires were analyzed with a 0.90 µm step for cross-section and a 0.60 µm step for longitudinal section mapping, respectively. From the EBSD data, the inverse pole figure (IPF) maps were evaluated using OIM 8 analysis software (EDAX, version 8, AME-TEC, Inc., Montvale, NJ, USA). The IPF maps were evaluated for the plane perpendicular and parallel to the extrusion direction (ED and ND, respectively).

Characterization of the Mechanical Properties
Mechanical behavior of the as-extruded wires was investigated from the point of view of a tensile test. First, while still on the spools, the wires were observed by the naked eye and a light microscope. This brief observation serves as the first preliminary check of the samples' shape, surface and other inhomogeneity, in order to avoid any premature failure given by some major defect of the specimen. For testing of the wire samples and definition of their gauge length for the proper setting of the tensile tests, stainless-steel capillaries were used. The samples were prepared from the spools in such a way that the samples' gauge lengths were defined by the crimping of these capillaries at both ends, thus preventing any further movement of the samples inside the capillaries. Therefore, the fully bored inner hole of the capillaries served as a guiding hole for the sample and simultaneously as the clamp, which was permanently enclosed by applying pressure from the outside by crimping pliers. Samples prepared in such way had, in all tests, a gauge length of~50 mm. The samples were then mounted on an in-house-designed and -built universal thermomechanical testing rig for macroscopic observation. The rig consisted of a loading frame, sample environment chamber, electrically conductive grips with active water cooling, a load cell with 45 N tension and compression capacity and a linear actuator controlled with a position magnetic sensor with a precision class of ±10 µm/m. The used environment chamber enabled control of the temperature in the range of liquid nitrogen to 200 • C. With the original purpose of using the Zn wires as a biocompatible and biodegradable material, we chose the body temperature (37 • C) as the testing temperature for all experiments. The tests were carried out at constant strain rates of the moving crosshead of 1 × 10 −1 %·s −1 . The parameters of the tests were controlled and recorded via a National Instruments cRIO system and closed-loop LabVIEW control system.

Starting Materials
The microstructure of the starting materials, i.e., the medium-grained (MG) and coarsegrained (CG) zinc annealed at 100 • C for 1 h and at 400 • C for 72 h, respectively, is shown in Figure 1. The MG zinc consisted of relatively equiaxed grains with a size of up to 1 mm. In contrast, the billets of the CG zinc were formed only by several grains with a size of several millimeters. Mechanical behavior of the as-extruded wires was investigated from the point of view of a tensile test. First, while still on the spools, the wires were observed by the naked eye and a light microscope. This brief observation serves as the first preliminary check of the samples' shape, surface and other inhomogeneity, in order to avoid any premature failure given by some major defect of the specimen. For testing of the wire samples and definition of their gauge length for the proper setting of the tensile tests, stainless-steel capillaries were used. The samples were prepared from the spools in such a way that the samples' gauge lengths were defined by the crimping of these capillaries at both ends, thus preventing any further movement of the samples inside the capillaries. Therefore, the fully bored inner hole of the capillaries served as a guiding hole for the sample and simultaneously as the clamp, which was permanently enclosed by applying pressure from the outside by crimping pliers. Samples prepared in such way had, in all tests, a gauge length of ~50 mm. The samples were then mounted on an in-house-designed and -built universal thermomechanical testing rig for macroscopic observation. The rig consisted of a loading frame, sample environment chamber, electrically conductive grips with active water cooling, a load cell with 45 N tension and compression capacity and a linear actuator controlled with a position magnetic sensor with a precision class of ±10 µm/m. The used environment chamber enabled control of the temperature in the range of liquid nitrogen to 200 °C. With the original purpose of using the Zn wires as a biocompatible and biodegradable material, we chose the body temperature (37 °C) as the testing temperature for all experiments. The tests were carried out at constant strain rates of the moving crosshead of 1 × 10 −1 %·s −1 . The parameters of the tests were controlled and recorded via a National Instruments cRIO system and closed-loop LabVIEW control system.

Starting Materials
The microstructure of the starting materials, i.e., the medium-grained (MG) and coarse-grained (CG) zinc annealed at 100 °C for 1 h and at 400 °C for 72 h, respectively, is shown in Figure 1. The MG zinc consisted of relatively equiaxed grains with a size of up to 1 mm. In contrast, the billets of the CG zinc were formed only by several grains with a size of several millimeters.

Extruded Zn Wires
The SEM micrographs of the chemically polished and etched surfaces of the prepared Zn wires are shown in Figure 2. It is clearly visible in Figure 2 that the grains were of equiaxed shape and that the grain size on the surface increased with increasing extrusion temperature. An influence of the grain size of the initial billet on the grain size of the extruded wires was observed as well. At the higher extrusion temperature (300 • C), larger grain sizes were observed in the case of the CG wires, while the smallest grain size was observed in the case of the CG wire extruded at 100 • C. The average grain size obtained by the image analyses of the surface micrographs is listed in Table 2. The SEM micrographs of the chemically polished and etched surfaces of the prepared Zn wires are shown in Figure 2. It is clearly visible in Figure 2 that the grains were of equiaxed shape and that the grain size on the surface increased with increasing extrusion temperature. An influence of the grain size of the initial billet on the grain size of the extruded wires was observed as well. At the higher extrusion temperature (300 °C), larger grain sizes were observed in the case of the CG wires, while the smallest grain size was observed in the case of the CG wire extruded at 100 °C. The average grain size obtained by the image analyses of the surface micrographs is listed in Table 2.  Table 2. Average grain size (in µm) obtained by the image analyses of surface micrographs ( Figure 2) and of the IPF maps (Figures 3-6).   grains with a certain orientation took place when the materials were extruded at 300 °C.

Sample
In the case of the CG_Ex 100 °C wire, a bimodal grain size was observed and this material was of the finest microstructure. None of the material possessed the basal fiber texture, which is a common texture for as-extruded Zn-based materials [24,25]. We also observed an influence of the microstructure of the initial material on the microstructure of the extruded wires. In the case of the MG wires, twins were observed in the microstructure of the materials extruded at both temperatures. For the CG wires, the common feature was that the large grains were often subdivided by low-angle boundaries.  In order to investigate the microstructure of the wire cores, cross-and longitudinal sections were prepared and analyzed by EBSD. Because pure zinc is very sensitive to any mechanical deformation and it can recrystallize even at low temperatures, the crossand longitudinal sections were prepared by ion machining using Xe FIB. This prevented the recrystallization of the materials during sample preparation. The obtained inverse pole figure (IPF) maps are shown in Figures 3-6. In these figures, it is clearly visible that the increasing extrusion temperature resulted in a larger grain size. Although the wires extruded at 300 • C were very coarse-grained and the statistics for the determination of the texture were very poor, the obtained results suggest that an abnormal grain growth of grains with a certain orientation took place when the materials were extruded at 300 • C. In the case of the CG_Ex 100 • C wire, a bimodal grain size was observed and this material was of the finest microstructure. None of the material possessed the basal fiber texture, which is a common texture for as-extruded Zn-based materials [24,25]. We also observed an influence of the microstructure of the initial material on the microstructure of the extruded wires. In the case of the MG wires, twins were observed in the microstructure of the materials extruded at both temperatures. For the CG wires, the common feature was that the large grains were often subdivided by low-angle boundaries.

Mechanical Behavior of the Zn Wires
The engineering tensile stress-strain curves of the prepared Zn wires are shown in Figure 7 and the values obtained from these curves are listed in Table 3. The tensile yield strengths (TYS) of all materials were very similar (39-46 MPa), but differences in the ultimate tensile strengths (UTS) were observed. The wires extruded at 300 • C reached lower UTS compared to their counterparts extruded at 100 • C. The wires extruded at 300 • C possessed UTS of around 66 MPa. Relatively large variations in the obtained UTS and elongations to fracture were observed (see Table 3). This points out the higher inhomogeneity of the wires extruded at 300 • C. The tensile stress-strain curves of these materials were serrated, suggesting that twinning took place during the deformation of these wires [26,27]. Regarding the wires extruded at 100 • C, higher TYS was reached in the case of the MG_Ex 100 • C wire; moreover, some serrations suggesting twinning were observed on the stress-strain tensile curves of the CG_Ex 100 • C wires.

Ability to Be Knotted
Because thin metallic wires are considered for the fabrication of absorbable sutures [21], it is important for the wires to be able to be knotted without any damage to the wire. In the case of the wires having serrated stress-strain curves, i.e., wires deformed by twinning, close tightening was impossible and the wires fractured. In the case of the MG_Ex 100 • C wire, we were able to tie the knot very tightly (see Figure 8).

Mechanical Behavior of the Zn Wires
The engineering tensile stress-strain curves of the prepared Zn wires are shown in Figure 7 and the values obtained from these curves are listed in Table 3. The tensile yield strengths (TYS) of all materials were very similar (39-46 MPa), but differences in the ultimate tensile strengths (UTS) were observed. The wires extruded at 300 °C reached lower UTS compared to their counterparts extruded at 100 °C. The wires extruded at 300 °C possessed UTS of around 66 MPa. Relatively large variations in the obtained UTS and

Ability to Be Knotted
Because thin metallic wires are considered for the fabrication of absorbable sutures [21], it is important for the wires to be able to be knotted without any damage to the wire. In the case of the wires having serrated stress-strain curves, i.e., wires deformed by twinning, close tightening was impossible and the wires fractured. In the case of the MG_Ex 100 °C wire, we were able to tie the knot very tightly (see Figure 8).

Discussion
As was clearly shown in Section 3.1, both extrusion temperature and initial microstructure can significantly influence the microstructure of the extruded wires. The increase in the grain size with increasing extrusion temperature was observed for both MG and CG initial Zn rods, and it can be simply explained by the decreasing Zener-Hollomon parameter, which decreases exponentially with the increasing extrusion temperature [24]. As is visible in Table 2, the grain size obtained from the SEM micrographs of the etched surfaces and from the EBSD data significantly differed. This can be explained in the following way: (i) the chemical etching does not highlight low angle boundaries and is not suitable for the distinguishing of neighboring grains with similar orientation. The wires extruded at 300 °C were strongly textured. Moreover, the CG_Ex 300 °C contained nu-

Discussion
As was clearly shown in Section 3.1, both extrusion temperature and initial microstructure can significantly influence the microstructure of the extruded wires. The increase in the grain size with increasing extrusion temperature was observed for both MG and CG initial Zn rods, and it can be simply explained by the decreasing Zener-Hollomon parameter, which decreases exponentially with the increasing extrusion temperature [24]. As is visible in Table 2, the grain size obtained from the SEM micrographs of the etched surfaces and from the EBSD data significantly differed. This can be explained in the following way: (i) the chemical etching does not highlight low angle boundaries and is not suitable for the distinguishing of neighboring grains with similar orientation. The wires extruded at 300 • C were strongly textured. Moreover, the CG_Ex 300 • C contained numerous low angle boundaries; therefore, the significantly larger grain size was observed on the surface of the wires extruded at 300 • C. (ii) The grain size on the surface should not necessarily reflect the grain size in the core of the wire. In our opinion, the grain size obtained from the EBSD data is more reliable and, based on them, we can conclude that CG wires possessed finer microstructures than the MG wires extruded at the same temperature. Moreover, the texture of the MG and CG wires differed. There could be several reasons for the influence of the initial grain size. (i) The initial grain size can influence the deformation mechanisms taking place during the extrusion. Coarse-grained materials are more sensitive to twinning or the formation of shear bands. Such microstructural defects can act as initiation sites for recrystallization and the formation of fine-grained bands, and chains can be expected in coarse-grained materials deformed at elevated temperatures [9,14,[28][29][30]. On the other hand, more intensive and homogeneous dynamic recrystallization is usually observed in the case of materials with finer microstructures. This is because a larger number of grain boundaries are present in fine-grained materials, and the grain boundaries act as nucleation sites for recrystallization. As a result, the newly recrystallized grain size is more homogeneous [14,30]. (ii) The CG billets were obtained by annealing at a large homologous temperature (0.97 of the melting point) for a long time period. This might lead to preferential grain growth. As a consequence, coarse grains with similar crystallographic orientation could occur in the CG material [31,32]. As a result, some deformation mechanisms could be prohibited in the CG zinc, and different recrystallization mechanisms could take place during the extrusion of the MG and CG Zn billets as a consequence. This subsequently results in differences in the grain size and texture of the wires.
The differences in the microstructure led to differences in the deformation behavior of the wires. The wires extruded at 300 • C tended to twin during the deformation, which is suggested by the serrated tensile stress-strain curves [26,27]. It is necessary to mention that the serrations could be observed also due to other effects, particularly due to the Portevin-Le Chaterilier effect [33] or due to the formation of cleavage cracks [34]. In our case, these effects can be excluded. The Portevin-Le Chaterilier effect takes place only for alloys, not for pure metals [33]. The formation of cleavage cracks would lead to a decrease in ductility compared to the materials which were deformed without the formation of cleavage cracks (MG_Ex 100 • C and CG_Ex 100 • C), but we observed comparable ductility for all wires. This makes the connection between the formation of cleavage cracks and the serration on the tensile curves improbable. The tendency towards twinning can be explained by the large grain size, which decreases the critical resolved shear stress (CRSS) for twinning [9,28]. Interesting findings were collected in the case of the wires extruded at 100 • C. Higher TYS and UTS were observed for the MG_Ex 100 • C, even though this wire possessed a significantly coarser microstructure than the CG_Ex 100 • C. The differences in TYS can be explained by the differences in texture and consequently by the differences in the Schmid factor for the basal slip (the predominant deformation mechanism in zinc [35]). The maps of the Schmid factor for the basal slip are shown in Figure 9. In the CG_Ex 100 • C, the majority of grains possessed a large Schmid factor for basal slip, while a large portion of grains in the MG_Ex 100 • C had a lower Schmid factor for the basal slip. This means that higher external stress was necessary to plastically deform the MG_Ex 100 • C wire. Moreover, the fine grains in the CG_Ex 100 • C can promote the non-slip deformation mechanisms, such as grain boundary sliding [9,13].
in zinc [35]). The maps of the Schmid factor for the basal slip are shown in Figure 9. In the CG_Ex 100 °C, the majority of grains possessed a large Schmid factor for basal slip, while a large portion of grains in the MG_Ex 100 °C had a lower Schmid factor for the basal slip. This means that higher external stress was necessary to plastically deform the MG_Ex 100 °C wire. Moreover, the fine grains in the CG_Ex 100 °C can promote the non-slip deformation mechanisms, such as grain boundary sliding [9,13]. In addition, serrations suggesting twinning were observed on the stress-strain curves of the CG_Ex 100 °C wires, which was very surprising because of the small grain size of this wire. Therefore, we performed an FIB cut near the fracture surface of the wires extruded at 100 °C after the tensile tests. The IPF and Schmid factor maps of these cuts are shown in Figure 10. Figure 10 clearly shows that strong grain coarsening took place during the deformation of the CG_Ex 100 °C wire. This was caused by a stress-strain-assisted grain growth. It could be attributed to the bimodal grain size of the CG_Ex 100 °C wire. It can be expected that the larger grains grew at the expense of the fine grains. As is shown in Figure 10d, a large portion of the overgrown grains possessed low values of Schmid factor for the basal slip. As a consequence of the combination of the large grain size and low value of Schmid factor, twinning possibly took place in the late stages of the deformation of the CG_Ex 100 °C wires (encircled area in Figure 7b). It should be also mentioned that only several grains were distributed over the diameter of the wires. This means that the wires could be considered as oligocrystals. This could explain why the wires reached slightly lower values of tensile strength and ductility compared to the pure extruded zinc studied in other works [13,36]-the so-called size effect [37,38]. It should be mentioned that the differences between the mechanical performance of the Zn wires and In addition, serrations suggesting twinning were observed on the stress-strain curves of the CG_Ex 100 • C wires, which was very surprising because of the small grain size of this wire. Therefore, we performed an FIB cut near the fracture surface of the wires extruded at 100 • C after the tensile tests. The IPF and Schmid factor maps of these cuts are shown in Figure 10. Figure 10 clearly shows that strong grain coarsening took place during the deformation of the CG_Ex 100 • C wire. This was caused by a stress-strain-assisted grain growth. It could be attributed to the bimodal grain size of the CG_Ex 100 • C wire. It can be expected that the larger grains grew at the expense of the fine grains. As is shown in Figure 10d, a large portion of the overgrown grains possessed low values of Schmid factor for the basal slip. As a consequence of the combination of the large grain size and low value of Schmid factor, twinning possibly took place in the late stages of the deformation of the CG_Ex 100 • C wires (encircled area in Figure 7b). It should be also mentioned that only several grains were distributed over the diameter of the wires. This means that the wires could be considered as oligocrystals. This could explain why the wires reached slightly lower values of tensile strength and ductility compared to the pure extruded zinc studied in other works [13,36]-the so-called size effect [37,38]. It should be mentioned that the differences between the mechanical performance of the Zn wires and bulk samples could be also caused by the differences in grain size and texture. The microstructural stability and the absence of twinning in the case of the MG_Ex 100 • C led to it displaying the best ability to be knotted. This is a very important property for its application as sutures on soft tissue or sutures used in sternum surgery [21]. We are aware that the strength of the prepared wires can be low and insufficient for surgical application. However, suitable alloying-for example, with magnesium-should allow significantly higher strengths to be achieved [39]. In general, suitable alloying leads to pinning of the grain boundaries and the achievement finer grain sizes after the extrusion. It should result in an increase in strength and ductility [13]. The design of malleable Zn-based alloys possessing high strength is the aim of our ongoing study.
displaying the best ability to be knotted. This is a very important property for its application as sutures on soft tissue or sutures used in sternum surgery [21]. We are aware that the strength of the prepared wires can be low and insufficient for surgical application. However, suitable alloying-for example, with magnesium-should allow significantly higher strengths to be achieved [39]. In general, suitable alloying leads to pinning of the grain boundaries and the achievement finer grain sizes after the extrusion. It should result in an increase in strength and ductility [13]. The design of malleable Zn-based alloys possessing high strength is the aim of our ongoing study.

Conclusions
In this work, we successfully prepared Zn wires by direct extrusion with an extremely huge extrusion ratio of 576:1. Based on the obtained results, several main conclusions can be drawn: i.
The extrusion process led to the preparation of wires whose texture did not correspond to the basal fiber texture, which is common for extruded Zn-based materials. ii.
An increase in the extrusion temperature resulted in an increase in grain size. iii.
The microstructure of the initial Zn billets strongly influenced the microstructure of the wires extruded at 100 • C. iv.
The as-extruded CG_Ex 100 • C possessed a bimodal grain size. This resulted in the stress-strain-assisted grain growth during the tensile test and a subsequent decrease in the ultimate tensile strength. v.
The obtained results suggest that the direct extrusion could be an effective method for the fabrication of Zn-based wires intended for surgical suture applications.
However, fine control of the final grain size and strengthening of zinc by alloying will be most likely necessary. Institutional Review Board Statement: Not applicable.
Informed Consent Statement: Not applicable.

Data Availability Statement:
The raw/processed data will be provided on request.