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14.02.2019 | Ausgabe 4/2019 Open Access

# Microstructure and Mechanical Properties of Copper Billets Fabricated by the Repetitive Extrusion and Free Forging Process

Zeitschrift:
Journal of Materials Engineering and Performance > Ausgabe 4/2019
Autoren:
Yang Wu, Shuhai Huang, Qiang Chen, Bo Feng, Dayu Shu, Zhiwei Huang
Wichtige Hinweise

## Publisher's Note

Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.

## Introduction

Pure copper and its alloys with the high electrical and thermal conductivity, high formability, machinability and relatively moderate properties are increasingly being concerned in many industries (Ref 1-3). However, pure copper ingots, prepared by casting, are composed primarily of coarse-grained (CG) microstructures (Ref 4). For some applications, these microstructures are not a problem because these applications do not depend on isotropic or superior mechanical properties, but for particular applications, it is important for the Cu to have ultrafine-grained (UFG) microstructures and extremely uniform mechanical properties. For instance, some of these applications include use as thin sheets for co-deformation with pure Cu for Nb3Sn superconductor diffusion barriers or as thick sheet disks for explosively formed penetrators (Ref 5). Without uniformity of microstructure, a weakened texture and a grain refinement microstructure, the characteristics of uniform deformation are absent and problems such as orange peel surface roughness, non-uniform thinning and premature facture can arise (Ref 6-8).
Ultrafine-grained materials have spawned much interest in fields where extremely high tensile and yield strength are necessary for construction, as an alternative to coarse-grained (CG) counterparts for satisfactory ductility (Ref 4, 9). A commonly used set of methods for fabricating UFG materials is the severe plastic deformation (SPD) methods, of which the best-known SPD techniques for producing UFG materials are the equal-channel angular pressing (ECAP) and the high-pressure torsion (HPT) (Ref 10-14). Various UFG SPD materials (e.g., Cu (Ref 15, 16), Al (Ref 17), Ta (Ref 18), Ti (Ref 19) and steel (Ref 6)) have been prepared using ECAP or HPT processing. Microstructures can be refined to equiaxed subgrains, which is accompanied by a significant increase with a satisfactory ductility. However, materials produced by ECAP and HPT have a small size along the transverse direction (Ref 20). This can limit the industrial applications of these methods for producing bulk billets for post-forging.
Extrusion and forging processes are suitable for preparing UFG materials at room or slightly above. It is well known that extrusion and free forging processes are highly efficient and simple, making them ideal for industrial applications. Therefore, we propose to combine these two traditional processes in cyclic processes of conventional direct extrusion and by free forging, a process termed repetitive extrusion and free forging (REFF). Compared with other SPD methods, REFF has several advantages, such as a higher strain per cycle, more shear planes and a more effective grain fragmentation. A similar approach, repetitive extrusion and upsetting (REU), has been reported by some publications (Ref 21). One publication reported the application of the REU process for fabricating pure aluminum billets with only 20 mm length along the longitudinal direction and 30 mm along the transverse direction. Unfortunately, this size of REU billets was insufficient to meet the needs of industrial applications. However, compared with REU, REFF has several advantages of a higher strain per cycle, a lower working force and no need for any additional tools or devices. Thus, REFF processing should be suitable for efficient and cost-saving industrial applications. In the present study, bulk size pure copper billets with excellent grain refinement microstructure for industry application, 80 mm in length along the longitudinal direction and 90 mm along the transverse direction, were successfully fabricated from coarse-grained pure Cu. Three cyclic REFF passes were achieved in this work. The microstructure, texture evolution and mechanical properties of the extrusion and forging of pure Cu from each REFF cycle pass were also systematically studied.

## Experiments and Methods

### REFF Process and Mechanical Tests

Commercially pure copper ingots containing coarse-grained (CG) counterparts and fully annealed condition were used for the fabrication of the UFG copper billets. As shown in Fig. 1, the CG pure copper was machined into a cylinder with 90 mm in diameter and 80 mm in length. This ingot was kept in a furnace at 660 °C for 2 h and then cooled at room temperature in order to obtain a complete recrystallized microstructure. Before testing, the billets were covered with lubricant zinc stearate and then were extruded at room temperature using an extrusion rate of 10 mm/s. The final extruded bar had a diameter of 50 mm. After complete extrusion, the extruded bar was free forged at the same rate until the initial diameter (90 mm) was reached again, so that the extrusion process could be repeated. For tensile tests, the dog-bone-shaped specimens with a gauge length of 35 mm and a diameter of 5 mm were cut along the longitudinal direction (ED or FD). Here, ED and FD refer to the extrusion direction and free forging direction, respectively. Tensile tests were performed on a Shimadzu mechanical testing system, using a strain rate of 10−3/s at room temperature. Each mechanical test was repeated three times.

### Characterization of Microstructure and Texture

For studying the structural evolution, samples were cut from the center of the specimen perpendicular to the compression plane and parallel to the ED and/or FD. The obtained surface was polished and subsequently etched. Electron backscattered diffraction (EBSD) analyses were conducted on a FEI Nova 400 SEM equipped with an HKL Chanel 5 system, using a step size of 1 μm for the initial CG Cu material and the first extrusion billets, 0.3 μm for the first forging billet and the second extrusion billets and 0.15 μm for the second forging billets. Each specimen was scanned at three different areas to measure the average grain size. The samples for EBSD mapping were mechanically ground, followed by electrochemical polishing for 7 s at 273 K in the electrolyte solution of 50% H3PO4, 25% distilled water and 25% alcohol at a DC voltage of 6.5 V. The EBSD data were analyzed using the Channel 5 software. Grain boundaries were identified using 2° minimum disorientation angle between two adjacent pixels, which led to the identification of grains having continuous closed boundaries with at least a 2° grain boundary angle. Grain orientations were then defined as the average of the pixel orientations constituting the grain, and then misorientation angle between adjacent grains was obtained using these average values (Ref 22).

## Results and Discussion

### Repetitive Extrusion and Free Forging Process

The present study shows that ultrafine-grained copper billet with bulk size for industry applications could be successfully fabricated from CG Cu ingots using the REFF process. During each cycle of the REFF process, a high effective strain and an average von Mises strain from the geometric dimensions of the die using the normal components of the strain tensor were obtained, as defined below (Ref 21):
$$\varepsilon = 4\ln \frac{D}{d}$$
(1)
For the extrusion process, the diameter of the initial CG copper ingot and the extruded UFG copper was replaced by D (90 mm) and d (50 mm), as shown in Fig. 1, respectively. Therefore, the extrusion ratio was 3.24, and the corresponding effective strain per REFF process was ε = 2.35. After two cycles, the sum effective strain became ε = 4.7. Because the strain value in the center position was very close to the strain value of calculation, and it generally increases from the center to the surface of the Cu billet, so the microstructure of the billet surface was preferentially refined (Ref 22). In order to obtain whether a homogeneous microstructure from the center to the surface of the billet had been obtained, samples for mechanical and microstructure testing were cut from the center of each billet, parallel to the extrusion or/and forging direction, respectively.

### Microstructure and Texture Evolution During the REFF Process

A fully annealed grain microstructure, as seen in the sample before REFF processing, is shown in Fig. 2. This structure includes a high fraction of annealing twins in the copper billet. The grains of CG copper were nearly equiaxed, and their average size was found to be about 50 μm, excluding twin boundaries. This was typical of a Cu microstructure after recrystallization. Before the REFF process, an equiaxed grain microstructure was obtained using fully annealing, in order to eliminate strain hardening and texture from previous metal working processes.
An EBSD analysis of the microstructure, crystallographic orientation maps and the misorientation angle distribution of the pure copper fabricated by the REFF process are shown in Fig. 3 and 4, respectively. The microstructures of the first extrusion and the first forging samples are displayed in Fig. 3(a) and (b), respectively. As seen in Fig. 3(a), an obvious elongation along the extrusion direction microstructure was obtained, so the initial annealed structure (Fig. 2a) gradually evolves into a pancake-like structure during the extrusion process. The edge dislocations and twin boundaries could not obviously be discerned from the elongation grains. However, following the subsequent forging step, these elongated grains transformed back into an equiaxed structure (Fig. 3b), which was different from the initial CG structure because of the large strain. During per cyclic REFF process, the strain path began with extrusion, and then it continued during forging, so the direction as well as the amount of strain was inverted and the grains recovered their initial shape. The strain-induced parallel dislocation walls and twin boundaries, formed by accumulation and rearrangement of dislocations and fragmentation of grains during the REFF process, are clearly shown in Fig. 3 and 4.
After the first extrusion process, a large number of low-angle boundaries (LABs) were present in the interior of the Cu grains (as shown in Fig. 3a). As illustrated in Fig. 3(b), after the first-cycle REFF process, the elongated grains were nearly all equiaxed shapes, and the LABs were still dominant in the interior of grains (as shown in Fig. 4b). Moreover, the initial grain boundaries could be observed clearly as inverse pole figure (IPF) EBSD maps. However, after the second cycle of the REFF process, the fraction of HABs increased in the extruded and forged samples (as shown in Fig. 4(c), (d) and Table 1). The average grain size, the number of interfaces per unit test line length PL and the stereology parameter SV are displayed in Table 1. The grain size measurement in the X and Y directions, parallel and perpendicular to the axis (ED/FD), respectively, was carried out using the linear intercept method without taking the twin boundaries into account. The grain-deformed matrix interface area density per unit volume SV is (Ref 23):
$$S_{\text{V}} = P_{{{\text{L}},X}} + P_{{{\text{L}},Y}}$$
(2)
$$P_{\text{L}} = N/L$$
(3)
$$d = L/N$$
(4)
Table 1
Average grain size, PL (in X and Y direction) and SV from EBSD analysis of the initial CG copper and post-REFF copper

Average grain size, μm
P L, X
P L, Y
S V
X direction
Y direction
Initial
44.1 ± 4
37.6 ± 3
0.023
0.027
0.05
First extrusion
25.4 ± 1.3
10.7 ± 1
0.039
0.093
0.13
First forging
2.6 ± 0.5
3.5 ± 0.5
0.38
0.29
0.67
Second extrusion
2.5 ± 0.15
2.3 ± 0.2
0.4
0.43
0.83
Second forging
0.8 ± 0.08
0.9 ± 0.06
1.25
1.11
2.36
The grain-deformed matrix interface area density per unit volume can be obtained by substituting Eq 3 and 4 into Eq 2 as follows:
$$S_{\text{V}} = 1/d_{X} + 1/d_{Y}$$
(5)
with the increasing strain, the recrystallization parameter SV increased gradually as shown in Table 1. This indicated directly that the fraction of HABs increased and grain refinement occurred. Refine equiaxed grains with an average grain size down to 0.8 μm appeared alongside subgrains as shown in Fig. 2(d). The majority of the small equiaxed grains in Fig. 2(d) were the red grains, with a <100> orientation, but most others had orientations <110> and <111> and were nearly maintained in the deformation matrix. Most of the initial grain boundaries had become fuzzier and curved compared to the sample fabricated by the first cyclic of the REFF process. This phenomenon was very similar to those found in pure copper and aluminum after tension deformed (Ref 24, 25). It was found that equiaxed cell structures and dense dislocation wall structures were observed in grains of different orientations in a polycrystal metal. For grains oriented near the [100], it appeared that the formation of these structures may be related to the fact that four-to-eight slip systems always have high and similar Schmid factors. However, the deformation matrix structures were always on the primary slip plane (11-1), which led to grains oriented near the [100] form predominantly an equiaxed structure, while other grains formed dense dislocation wall structures more easily.
The main mechanism of grain refinement using REFF was the elongation of grains during extrusion, which were fragmented by the maximum tangential stress that was produced by shearing on the slip lines during free forging (Ref 21). During a cycle of the REFF process, as shown in Fig. 3 and 4, in order to match the plastic strain produced by SPD, a suite of slip systems were activated in the interior of grains, which led to a large amount of LABs and dislocation boundaries. The generation of new boundaries, including LABs and dislocation boundaries inside a grain could be interaction with the increase in strain. After two passes of the REFF process, the elongated structure in the extruded copper billet, as shown in Fig. 3(a), was replaced by a structure predominantly consisting of free forging billets with small equiaxed grains (as displayed in Fig. 3d). With an increase in the strain, the density of dislocation continued to increase and the LABs absorbed dislocation and increased their misorientation due to rise in the fraction of HABs and the formation of new finer grains, leading to grain refinement (Ref 26). However, the dislocation activities in the interior of finer grains became more difficult in this condition. Subgrain rotation, leading to an increase in the misorientation and an increase in the fraction of HAGs and grain refinement, occurs to accommodate such plastic deformation. Otherwise, the <100> orientation grains became subdivided by ordinary dislocation cell boundaries defining a three-dimensional cell structure (Ref 27). This orientation of grains would lead to more homogenous grain size compared to others because of the dynamic recrystallization.
The evolution of the crystallographic texture and the volume fractions of the fiber textures, in the form of inverse pole figures of the longitudinal direction (parallel to ED or FD) samples axis, are displayed in Fig. 5. The fully annealed CG copper samples have a relatively weak texture, with mixed <100> + <111> fibers parallel to the longitudinal direction. After the first cycle of the REFF process, a different fiber texture was obtained. Through the extrusion pass, the <111> fiber was strengthened significantly, and the <100> fiber texture was nearly absent. However, the <111> texture produced during the extrusion zone completely disappeared by the following free forging process, giving rise to the <110> fiber texture. At later cycles of the REFF process, the <111> texture and the <110> texture alternately appeared in the UFG pure copper samples. Compared to the first-cycle samples, the <111> fiber texture produced during extrusion process was evidently weakened and the <100> texture was relative stabilized low value data after the second extrusion. However, the <110> texture generated during free forging process was significantly strengthened.
The casting texture during a continuous unidirectional solidification process largely depends on the crystal structure of the material. It is known that the preferential growth orientation of face-centered cubic (fcc) copper is <100> (Ref 27). As can be seen in Fig. 5, the coarse-grained copper mainly grew along the <100> direction. After the REFF process, because the <111> fiber is known as the extrusion texture of fcc metals, and the <110> fiber texture is the characteristic for compression texture (Ref 22), the production of <111> fiber during the extrusion process was very evidently reduced following the free forging process, giving rise to the <110> fiber. The opposite texture evolution produced in the extruded and forged sample was due to the complete inversion of the strain of the extrusion and free forging process. Therefore, the <111> fiber texture generated during the extrusion process was replaced by the <110> fiber texture produced during the forging process. Otherwise, the interaction of the opposite texture components led to a weakened texture UFG copper billet for post-forging.

### Mechanical Behavior of Extruded and Free Forged Copper

The results of microhardness tests for the extruded and free forged specimens are displayed in Fig. 6. After the first extrusion process, the microhardness of the fully annealed copper increased sharply from 63 to 114 HV. This was due to an increase in the work hardness. However, at the end of the first REFF cycle, the hardness exhibited only a slight increase, from 114 to 122 HV. A maximum value of hardness 131 HV was observed at the end of the second extrusion process. Some possible mechanisms of the improvement in hardness of the SPD copper fabricated by the REFF process from CG copper are discussed below. For CG pure copper, the stereology parameter SV was smaller than SPD samples as shown in Table 1. Therefore, the volume density of high-angle grain boundary, a barrier for dislocations motion, increased with increasing strain. The CG copper structures had a weak resistance to the dislocation motion, and slip system could move easily, resulting in the softening of the microhardness. After the cyclic REFF process, several grain fragmentation and orientation led to more defects. An increase in the density of dislocations and HABs (as shown in Fig. 4) during SPD, resulting in the dislocation movement being resisted in the hardness test, led to an increase in microhardness. Finally, the hardness was slightly reduced after the end of the third cycle of the REFF process. This was due to dynamic recovery and recrystallization.
Figure 7 and Table 2 show the true stress–strain curves of the copper fabricated by the REFF process. The CG sample showed high ductility and low yield strength. After the REFF process, the ultimate tensile strength (UTS) and yield strength (YS) of all samples were remarkably increased. The UTS and YS values of the copper after two cycles REFF process were 451 and 462 MPa, respectively. The samples retained a sufficient ductility of 8.3%. The REFF process combines two strengthening mechanisms: grain boundary strengthening and dislocation strengthening. In fact, increasing dislocation contributed to the improvement in the tensile strength. Moreover, the fine grains resulting from the REFF process helped to maintain a sufficient ductility even after a significant straining from the cold REFF processing. On the other hand, the increase in the elongation in the extrusion billets, compared with the free forged ones, was due to a lower decrease in the work hardening rate when the stress increased. In order to study the pure copper billets possessing fast necking behavior after each REEF process, the fracture surface was evaluated using SEM. These results are shown in Fig. 8. It was obvious that a relatively flat zone could be observed adjacent to a dimple zone, which was the typical fracture characteristic for Cu. However, compared with CG copper, the fracture surface in the second cycle REEF samples mainly consisted of dimples with a number of cleavage planes that exhibit typical toughness fracture character. This led to sufficient ductility and a fast necking phenomenon.
Table 2
The yield strengths, ultimate strengths and elongations due to fracture under tension along the longitudinal direction
Samples
Yield strength, MPa
Ultimate strength, MPa
Elongation, %
Initial annealed
79 ± 2
241 ± 1
42.5 ± 3
First extrusion
334 ± 4
345 ± 2
8.8 ± 1
First forging
361 ± 3
370 ± 4
9.4 ± 1
Second extrusion
407 ± 4
415 ± 2
7.9 ± 0.8
Second forging
451 ± 2
462 ± 1
8.3 ± 1.3

## Conclusion

In the present study, copper billets for mass applications were successfully and efficiently fabricated by REFF, without using any additional tools or devices. Several conclusions were reached as follows:
1.
After two cycles of the REFF process, the sum effective strain was ε = 4.7. The average grain size was measured to be 0.8 μm.

2.
The <111> texture and <110> texture alternately appeared in the pure copper samples during the REFF process. This was beneficial for obtaining a weakened texture microstructure in the Cu billets.

3.
The yield strength of samples was remarkably increased to 462 MPa after two cycles of the REFF process, and the samples retained a sufficient ductility of 8.3%.

## Acknowledgments

This research is funded by Chongqing Research Program of Basic Research and Frontier Technology (No. cstc2015jcyjBX0115) and Guangdong Academy of Science Fund (2018GDASCX-0967).

## Publisher's Note

Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.

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