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Effect of annealing time on bending performance and microstructure of C19400 alloy strip

  • Yanmin Zhang EMAIL logo , Baohuan Huang , Hongjiao Gao , Shanguang Li , Fei Zhou and Kexing Song
Published/Copyright: August 29, 2024
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Nanotechnology Reviews
From the journal Nanotechnology Reviews Volume 13 Issue 1

Abstract

The effect of annealing time on the bending properties and microstructure of cold-rolled C19400 alloy was studied by transmission electron microscopy, scanning electron microscopy, and optical microscopy. With the increase in annealing time, the bending properties of the alloy first increased and then decreased, and the elongation increased from 8.33% in cold-rolled state to 11.58% after annealing for 60 min, which increased by 39.02%, and then decreased to 10.0% after annealing for 90 min. Within the experimental range, the bending performance is the best when the annealing time is 60 min. When the relative bending radius is 0.4, the outer surface of the bending part of the alloy changes from a large number of microfine cracks before annealing to the disappearance of cracks after annealing. The analysis shows that the decrease in the dislocation density, the ordering of the dislocation structure, and the refinement of the precipitated phase are the keys to improving the bending performance of the strip after annealing.

Keywords: C19400 alloy; bending performance; dislocation density

1 Introduction

Copper alloy is widely used in the field of high-end connectors due to its excellent transmission performance and comprehensive mechanical properties [1,2]. In recent years, with the rapid development of electronic communication technology in aerospace, new energy vehicles, 5G communication, and other fields, higher requirements have been put forward for connectors that play a key role in signal transmission. In addition to higher reliability and a stronger ability to transmit a large current, the development of connectors is moving toward miniaturization and precision. The materials used in connector products need to have good formability while satisfying strength and conductivity requirements [3,4]. Due to the complex structure of the connector product, the material needs to be bent and deformed during production. With the precision and miniaturization of connector products, the requirements for the bending radius of the products are becoming increasingly smaller, and the bending performance has gradually become one of the important indicators for evaluating connector materials [5].

Microstructures such as dislocation and precipitated phase characteristics are the key factors affecting the bending properties of the alloy. The microstructure of the alloy is often adjusted by an annealing process to improve the bending properties of the alloy and even improve the comprehensive mechanical properties of the alloy [6,7,8,9]. Castany et al. [10] studied the effect of the size and distribution of grain boundary precipitates on the bending properties of materials through different heat treatment processes and linked the bending properties with the microstructure. The study found that the size of the precipitates is closely related to the bending properties of the AA6016 aluminum alloy sheet. Large AlFeSi particles exist in the shear band, which easily leads to the generation and expansion of cracks. In addition, the density of grain boundary precipitates has no effect on the generation and propagation of cracks. Qin et al. [11] studied the effect of microstructure on the properties of Al–Zn–Mg by heat treatment. The results show that the smaller the size of the precipitated phase (MgZn2) and the larger the spacing, the stronger the ability of the macroscopic crack to expand during the deformation of the alloy. Hoseini et al. [12] studied the bending properties of AM50 alloys with different compositions. The results show that the bending properties of the alloys are affected by the morphology and size of the precipitated phase. The presence of the second phase material with coarse size easily causes crack initiation and propagation. Lee et al. [13] studied the effect of dislocation density on the bending properties of an AZ80 alloy and found that a decrease in dislocation density is more conducive to the deformation of the alloy and that the bending properties are improved.

The above studies show that microstructure characteristics such as dislocation density and the size of the precipitated phase have a significant effect on the bending properties of the alloy, and the key to improving the bending properties of the alloy is to regulate the microstructure. Therefore, it is very important to select the appropriate annealing process to adjust the microstructure of the alloy strip to improve the bending performance of the strip. There are few studies on the influence of microstructure evolution of C19400 alloy on its bending performance, and the influence mechanism on bending performance is still unclear and needs further study.

Therefore, this article takes the widely used connector material cold-rolled C19400 alloy as the research object, studies the influence of annealing time on the properties and microstructure of the alloy, studies the internal relationship between microstructure and properties, and explores the influence mechanism of microstructure characteristics on the bending performance of the strip, which provides theoretical guidance for the preparation of copper alloy strips for high-end connectors.

2 Test materials and methods

2.1 Test materials and annealing treatment

The test material is a C19400 alloy strip with a cold-rolled thickness of 0.4 mm that was ordered from a manufacturer. The chemical composition of the alloy is shown in Table 1.

Table 1

Chemical composition of the C19400 alloy (%, mass fraction)

Element P Fe Pb Zn Cu
Content 0.03 2.18 ≤0.001 0.1 Bal.

An STGK-100-12 vacuum atmosphere tube resistance furnace was used for annealing treatment. The annealing temperature was 350°C, and the annealing time was 30, 60, and 90 min. After the annealing treatment, a rectangular bending specimen with a length of 60 mm and a width of 25 mm was cut.

2.2 Bending experiment

The 90° V-shaped bending experiment was carried out on a self-designed multifunctional testing machine. The bending direction is longitudinal (GW), that is, perpendicular to the rolling direction (RD), and the bending radius is 0.16 mm, as shown in Figure 1. Design and process a bending die with a bending radius of 0.16 mm, and the structure of the bending die is shown in Figure 2. The bending punch is installed on the die seat of the testing machine, and the female die is fixed on the workbench of the testing machine. The up-and-down movement and position of the punch are adjusted by microcomputer control. Wipe the blank with anhydrous alcohol before the test to prevent impurities on the surface from affecting the results, and put it in the middle of the female die. To ensure the stability of the loading force, the average loading speed during the test is 40 mm/s. After the material is fully bent and kept for 10 s, the equipment returns, the male die rises, and the material is taken out.

Figure 1 V-shaped bending multifunctional testing machine.
Figure 1

V-shaped bending multifunctional testing machine.

Figure 2 Bending mold structure drawing.
Figure 2

Bending mold structure drawing.

2.3 Performance testing

The mechanical and electrical properties of the cold-rolled and heat-treated alloys before bending were tested. The electrical conductivity was tested by Sigma2008B1 portable digital eddy current metal conductivity meter. Tensile tests were performed at room temperature along the rolling direction (RD) using a WDW-100D microcomputer-controlled electronic universal testing machine.

After bending, the sample was scanned by a scanner to obtain an image that was imported into Auto CAD software to measure the angle after springback [14], and the springback amount was obtained. Under the same test conditions, the springback amounts for multiple bending tests were determined, and the average value of the results was taken as the final test result.

2.4 Microstructure observation

The outermost area of the along the rolling direction (RD) and the vertical rolling direction (TD) sections before bending under different processes was observed. The observed parts were ground and polished, corroded with ferric nitrate hydrochloric acid solution, and characterized by a Shunyu ICX41 M inverted metallographic microscope. The observation sites of transmission electron microscopy (TEM) and scanning electron microscopy (SEM) are shown in Figure 3. The morphology of the outer surface after bending was observed by SEM; that is, cross sections of RD and TD and defects such as cracks on the outer surface of the deformation zone were observed. The RD and ND cross-sections of the bent specimens were prepared by a focused ion beam (FIB). The lift-out processing method was used, and the sampling process was as follows: a slice of 4 μm × 4 μm × 70 nm was taken down vertically from the surface of the sample, the specific sampling process is shown in Figure 4. An FEI Talos F200× high-resolution transmission electron microscope was used to characterize the microstructure morphology and precipitated phase.

Figure 3 Sampling position maps.
Figure 3

Sampling position maps.

Figure 4 FIB sampling process.
Figure 4

FIB sampling process.

3 Experimental results and analysis

3.1 Results of the performance test

Figure 5 shows the performance test results of the C19400 alloy strip with different annealing times. It can be seen from the diagram that the annealing time has a significant effect on the mechanical properties of the C19400 alloy but has no obvious effect on the electrical conductivity. From cold rolling to annealing for 30, 60, and 90 min, the electrical conductivity is 51.98, 52.4, 52.87, and 52.19% IACS, respectively, which remains basically unchanged. The tensile strength of the cold-rolled alloy is 459.2 MPa. When the annealing time is 30 min, the tensile strength decreases to 437.6 MPa. When the annealing time is 60 min, the tensile strength decreases to 434.2 MPa. When the annealing time is 90 min, the tensile strength is increased by 14.4 MPa compared with the annealing time of 60 min. The elongation of the cold-rolled alloy is 8.33%, and when the annealing time is 30 and 60 min, it is 11.67 and 11.58%, respectively. When annealed for 90 min, the elongation is 10.0%. The overall elongation first increased and then decreased. This is because a large number of plastic deformation occurs in the rolling process, resulting in a large number of dislocations gathering. With the extension of annealing time, the dislocation density gradually decreases, and the deformation resistance of the material decreases with the decrease in dislocation density, which makes it easier to slip during deformation. Therefore, the strength is reduced and the plasticity is improved.

Figure 5 Performance test of C19400 copper alloy strips annealed for different lengths of time.
Figure 5

Performance test of C19400 copper alloy strips annealed for different lengths of time.

Figure 6 shows the springback after annealing at different times. With increasing annealing time, the amount of springback gradually decreases. The springback is 12.5° in the cold rolling state. When the annealing time is 30 min, the springback decreases to 10.3°. When the annealing time increased from 30 to 60 min, the springback amount tended to be gentle, and the springback amount decreased to 10.1°, only decreasing by 0.2°. As the annealing time continued to increase, the springback amount continued to decrease. When the annealing time was 90 min, the springback amount decreased by 26.4% before and after annealing. Under the same deformation, the springback after annealing decreases, because with the extension of annealing time, the grain structure of the alloy is gradually uniform, and the slip system is easier to move, which is more conducive to plastic deformation.

Figure 6 Springback amount of strips annealed at different times.
Figure 6

Springback amount of strips annealed at different times.

3.2 Microstructure analysis

Figure 7 shows the grain structure of the C19400 alloy under different annealing times. Figure 7(a) shows that the grains of the cold-rolled C19400 alloy are elongated along the rolling direction, which is because the cold deformation during the rolling process causes a large plastic deformation of the strip. When the annealing time is 30 min, the grain structure is still a long strip fiber structure distributed along the rolling direction, and there are many fine equiaxed grains near the rolling streamline, as shown in Figure 7(b). This is because, during the cold rolling process, a large amount of deformation provides deformation energy for the strip, thereby increasing the driving force of recrystallization. After annealing, the strip releases part of the energy, which provides nucleation energy for the broken grains after rolling, so that the strip recrystallization occurs [7,15]. The annealing time continues to increase. When the annealing time is 60 min, the grains are not obvious along the rolling direction, the grain boundaries increase, the equiaxed grains increase, and the grain size decreases, as shown in Figure 7(c). Figure 7(d) shows the grain structure annealed for 90 min; the grain size increases, the annealing time increases, and the recrystallized grain grows. The recrystallization process of the alloy strip is fully carried out from the cold rolled state to annealing for 30 and 60 min, and the number of recrystallized grains in the microstructure increases. The equiaxed grains replace the long strip of fibrous grains, and the annealing time continues to increase the grain growth. With increasing annealing time, the grain structure of the strip before bending shows a trend of decreasing first and then increasing. When the annealing time is 60 min, the recrystallization process causes the disappearance of the work-hardening phenomenon and the disappearance of a large number of dislocations. This is because the existence of the thermal activation energy promotes the rearrangement of the dislocation structure inside the alloy and the softening of the strip [8,16].

Figure 7 Grain structure of strips annealed at different times. (a) Cold rolled; (b) 30 min annealed state; (c) 60 min annealed state; and (d) 90 min annealed state.
Figure 7

Grain structure of strips annealed at different times. (a) Cold rolled; (b) 30 min annealed state; (c) 60 min annealed state; and (d) 90 min annealed state.

3.3 Surface morphology observation after bending

Figure 8 shows the surface morphology of the C19400 alloy strip after bending for different annealing times under SEM when the relative bending radius is 0.4. After bending the cold-rolled alloy, a large number of cracks appear on the surface. The crack mainly exists in the form of a network, and the direction of the crack is 45° with the rolling direction, as shown in Figure 8(a). Figure 8(b) shows the surface morphology of the strip after bending and annealing for 30 min, and the number of cracks is significantly reduced. Figure 8(c) shows the surface morphology of the strip after bending and annealing for 60 min. The surface is relatively flat, no cracks are observed, and the surface quality of the strip is improved. Figure 8(d) shows the surface morphology of the strip after bending and annealing for 90 min, and small microcracks can be observed. The surface quality of the strip is lower than that of annealing for 60 min. Compared with the cold-rolled alloy, the surface defects of the alloy annealed for 30 and 60 min are improved after bending, and the surface quality is continuously improved. When the annealing time is increased to 90 min, the surface quality shows a downward trend. When the annealing time is 60 min, the bending performance is the best, and the mechanical and electrical properties meet the requirements of use. Therefore, the improvement process of bending performance in the process of annealing for 30 and 60 min is analyzed emphatically. It can be seen from the mechanical properties test that the plasticity of the alloy annealed for 30 min is slightly better than that of the alloy annealed for 60 min, but the bending performance is the best at 60 min because the bending performance of the alloy is also affected by the grain size, texture type, and other factors.

Figure 8 Grain structure of strips annealed at different times. (a) Cold rolled; (b) 30 min annealed state; (c) 60 min annealed state; and (d) 90 min annealed state.
Figure 8

Grain structure of strips annealed at different times. (a) Cold rolled; (b) 30 min annealed state; (c) 60 min annealed state; and (d) 90 min annealed state.

3.4 Analysis of microstructure characteristics

Figure 9 shows the TEM diagram of the microstructure of the C19400 copper alloy sheet with different annealing times. It can be seen from the figure that the dislocation density decreases with increasing annealing time, and the size of the precipitated phase decreases. For the cold-rolled alloy, due to a large amount of plastic deformation during the rolling process, a large number of dislocations accumulate, and the precipitated phase appears at the boundary of the high dislocation density region but does not pass through the high dislocation density, which hinders the movement of dislocations, as shown in Figure 9(a). When the annealing time is increased to 30 min, the microstructure of the alloy is shown in Figure 9(b), and the dislocation density in the high dislocation density region is significantly reduced. Figure 9(c) shows the microstructure of the alloy when the annealing time is 60 min. It can be seen from the figure that the decrease in dislocation density can be seen in the precipitates and the obvious interface. The deformation resistance of the material decreases with decreasing dislocation density, and it more easily slips in the process of deformation. Therefore, the strength decreases and the plasticity increases [17,18].

Figure 9 TEM morphology after bending of strips annealed at different times. (a) Cold rolled; (b) 30 min annealed state; and (c) 60 min annealed state.
Figure 9

TEM morphology after bending of strips annealed at different times. (a) Cold rolled; (b) 30 min annealed state; and (c) 60 min annealed state.

Figure 10 shows the TEM morphology of the cold-rolled C19400 copper alloy strip after bending. After the cold rolled alloy is bent, it can be seen that there are high dislocation density regions and some low dislocation density regions, and the dislocation distribution is disordered. A spherical precipitated phase with a size of approximately 75 nm is seen at the boundary. The precipitates block the movement of the dislocation, as shown in Figure 10(a). In Figure 10(b), a coarse precipitated phase with a size of 119.9 nm was observed. The dislocation was blocked near the precipitated phase, and the dislocation was bent. The cold-rolled strip exhibits a coarse precipitated phase with a size of 75–180.3 nm, as shown in Figure 10(c). Figure 10(d) shows the dark field image in the enlarged area of Figure 10(e), and there are precipitated phases with different sizes, which hinders the movement of dislocation. The size of the precipitated phase in Figure 10(e) is 180.3 nm, and the diffraction pattern of Figure 10(f) is obtained. The composition of the ellipsoidal precipitated phase was γ-Fe.

Figure 10 TEM morphology after bending of strips annealed at room temperature. (a)–(c) Dislocation and precipitated phase; (d) partially amplified regional dark field image; (e) bright field image; and (f) diffraction pattern calibration.
Figure 10

TEM morphology after bending of strips annealed at room temperature. (a)–(c) Dislocation and precipitated phase; (d) partially amplified regional dark field image; (e) bright field image; and (f) diffraction pattern calibration.

Figure 11 shows the TEM morphology of the 30 min annealed C19400 strip after bending. It can be observed from Figure 11(a) that the dislocation density is significantly reduced. When the plastic deformation reaches a certain degree, the slip system opens, and the dislocation moves and gradually becomes regular. The dislocation structure becomes ordered, as shown in Figure 11(b). It can be observed from Figure 11(c) that fine second-phase particles appear around the dislocation line.

Figure 11 TEM morphology after bending of strips annealed for 30 min. (a) Dislocation and precipitated phase; (b) dislocation; and (c) second phase.
Figure 11

TEM morphology after bending of strips annealed for 30 min. (a) Dislocation and precipitated phase; (b) dislocation; and (c) second phase.

Figure 12 shows the TEM morphology of the annealed C19400 strip after bending for 60 min. Figure 12(a) shows that the dislocation density is greatly reduced and that there is a fine second-phase material. According to Figure 12(b), a precipitated phase is observed near the dislocation after 60 min of annealing. When the moving dislocation line meets the precipitated particles, the dislocation bends and forms an arc-shaped structure, and the dislocation movement is blocked. The dark field image of Figure 12(c) shows a spherical second phase with a size of approximately 50–60 nm.

Figure 12 TEM morphology after bending of strips annealed for 60 min. (a) Dislocation and precipitated phase; (b) bright field image; and (c) dark field images.
Figure 12

TEM morphology after bending of strips annealed for 60 min. (a) Dislocation and precipitated phase; (b) bright field image; and (c) dark field images.

The size and distribution of the second-phase particles in the matrix play a key role in recrystallization nucleation [7,19]. According to the analysis of Figures 11 and 12, when the annealing time increases to 30 and 60 min, the decrease in the size of the second phase precipitates reduces the obstruction effect on grain boundary movement, which is more conducive to the occurrence of the grain recrystallization process. With decreasing dislocation density, the resistance to plastic deformation is weakened, which is more conducive to the occurrence of deformation. With the presence of a small precipitated phase, the hindrance to dislocation movement is reduced, grain slippage occurs more easily in the deformation process, and the bending performance of the alloy is improved.

4 Discussion

4.1 Effect of annealing time on the bending properties of the alloy

After annealing treatment, the microstructure shows a decrease in dislocation density and the presence of small precipitates. There are a large number of dislocations in the cold-rolled alloy, which is due to the large amount of plastic deformation during the cold-rolling process, and the dislocations are arranged and distributed in a disordered manner. During the annealing process, the dislocations in the crystal move under the action of the thermal effect. When two opposite dislocations are at the same point, the dislocations disappear [20,21]. With the extension of annealing time, the thermal activation effect causes the rearrangement of dislocations in the alloy structure and leads to the annihilation of a large number of dislocations [22,23]. The disappearance of a large number of dislocations leads to the weakening of the deformation resistance of the material and the phenomenon of annealing softening, which is manifested as decreased strength and increased elongation [24]. The ordering of the internal dislocation structure makes it easier for the material to slip during plastic deformation and promotes the occurrence of the deformation process. After bending deformation, combined with Figure 7, the surface morphology after bending is improved, and the bending performance is obviously improved. The effect of dislocation density on the properties of the alloy is much greater than that of grain size. With the occurrence of the recrystallization process, the average grain size decreases. In general, grain refinement strengthens the alloy. However, the strength of the alloy annealed at 350°C for 60 min is lower than that of the cold-rolled alloy.

The full name of KAM is kernel average misorientation, which describes the local misorientation. The value of local misorientation represents the average misorientation between adjacent points, which reflects the uniformity of plastic deformation of materials. The higher the value, the higher the degree of uneven plastic deformation or the higher the defect density. Polycrystalline grains have anisotropy and random orientation, and non-uniform plastic deformation occurs during bending deformation, resulting in local strain inside the grains. The density of geometrically necessary dislocations (GNDs) inside a material is measured by the local mean disorientation diagram, as shown in Figure 13. The higher the density of the GND is, the greater the degree of non-uniform plastic deformation will be and the more serious the strain concentration will be. The GND density of the alloy under different conditions is calculated to judge the degree of homogenization of plastic deformation. Its calculation formula is

(1) ρ mean GND = 2 KAM ave μ b ,

where ρ mean GND represents the geometric necessary dislocation density; KAM ave is the average value of KAM; μ represents the scanning step size of EBSD; and b is the Bergdahl vector.

Figure 13 Distribution map of local average misorientation and GNDs after bending of strips annealed at different times. (a) and (b) Cold rolled and (c) and (d) 60 min annealed state.
Figure 13

Distribution map of local average misorientation and GNDs after bending of strips annealed at different times. (a) and (b) Cold rolled and (c) and (d) 60 min annealed state.

The C19400 alloy is a face-centered cubic structure, and its crystal structure Burgers vector is a/2 〈110〉. The geometric necessary dislocation density value is calculated by KAM. Substituted into the formula, the internal geometric necessary dislocation density of the cold-rolled alloy material is 2.088 × 1,016 m−2. After annealing for 60 min, the geometric dislocation density of the material was 1.794 × 1,016 m−2, which decreased by approximately 14.08%. After annealing, the plastic deformation of the alloy is more uniform. According to the analysis, under this annealing condition, the dislocation density of the alloy decreases, so the overall softening after annealing is more conducive to the occurrence of the plastic deformation process, and the bending performance of the alloy is improved accordingly.

Figure 14 shows the TEM morphology after annealing for 90 min. When the annealing time increased from 60 to 90 min, the dislocation density increased, the coarse spherical precipitated phase was observed, and the size was close to 100 nm. The increase in dislocation density plays a strengthening role, the movement of dislocations is more difficult, and the ability of metal to resist plastic deformation is increased, which is manifested as an increase in material strength. The size of the precipitated phase is coarse, the nailing effect impedes the movement of dislocations, and in the bending deformation process, it easily causes the generation and development of cracks. The increase in dislocation density and the coarse size of the precipitated phase are the main reasons for the increase in material strength and the decrease in bending performance during 90 min of annealing.

Figure 14 TEM morphology after bending of strips annealed for 90 min. (a) Dislocation and (b) precipitated phase.
Figure 14

TEM morphology after bending of strips annealed for 90 min. (a) Dislocation and (b) precipitated phase.

Due to the presence of coarse precipitated phase particles, the alloy exhibits poor bending properties. In the process of deformation, cracks are easily generated near the coarse precipitated phase and propagate along the grain boundaries [11,12]. According to the analysis of Figures 9, 11 and 13, the size of the precipitated phase in the cold-rolled alloy is coarse. After annealing for 60 min, a fine precipitated phase is observed, and the bending performance of the alloy is improved. The annealing time continues to increase to 90 min, the large precipitated phase exists, and the bending performance decreases. After annealing for 60 min, the size of the precipitated phase is small, which effectively avoids the generation and propagation of cracks. After annealing for 90 min, the precipitated phase is coarse, the dislocation density is increased, and the plastic deformation ability of the alloy is weakened, which is manifested by the increase in the strength of the material and the decrease in the bending performance. After annealing for 60 min, the dislocation density decreases, the dislocation structure becomes more orderly, and the precipitated phase size is small, which is an improvement in the bending performance of the strip.

4.2 The effect of annealing time on the mechanical and electrical properties of the alloy was studied

Figure 5 shows that the annealing time has little effect on the conductivity of the alloy but has a significant effect on the mechanical properties. When the annealing time is 60 min, the tensile strength decreases by 25 MPa, and the elongation increases from 8.33 to 11.58%. After annealing at a lower temperature, the external thermal activation energy will be enhanced, thereby promoting the thermal vibration of the atoms. As the amplitude increases, the binding force between the atoms decreases, and the resistance of the dislocation motion also decreases, which makes the dislocation motion easier to move. The dislocation movement is relatively easy, thus reducing the tensile strength of the material. The GND density is calculated by KAM. The internal geometric necessary dislocation density of the cold-rolled alloy material is 2.088 × 1,016 m−2, and the geometric dislocation density of the material after annealing for 60 min is 1.794 × 1,016 m−2. The geometric dislocation density decreased after annealing. The decrease in dislocation density leads to the weakening of the deformation resistance of the material. In the process of deformation, it is easier to slip. Therefore, the strength decreases and the plasticity increases. After annealing for 90 min, the dislocation density increases, and the presence of large precipitates hinders dislocation movement, which is an important reason for the increase in alloy strength and the decrease in plasticity.

5 Conclusion

After annealing treatment, the bending performance of the strip is improved. Within the test range, the alloy has the best bending performance when annealing for 60 min. When the relative bending radius is 0.4, the surface morphology of the alloy changes from a large number of cracks in the cold rolled state to no cracks. Low temperature annealing has a great influence on the mechanical properties of the strip, but has little effect on the electrical conductivity. With the extension of annealing time, compared with the cold rolled state, the tensile strength of the strip decreases and the elongation increases.

After the annealing treatment of the alloy, the dislocation density inside the material decreases, the dislocation structure is ordered, and the second phase precipitated substances are fine. In the process of deformation, the alloy is more conducive to the occurrence of plastic deformation, which is the main reason for the improvement in the bending performance of the alloy.

Acknowledgments

The authors express gratitude to the National Natural Science Foundation of China (52373313), the Ningbo Innovation Consortium Project (2021H003), and the Henan Province Major Science and Technology Project (221100210300).

  1. Funding information: The National Natural Science Foundation of China (52373313), the Ningbo Innovation Consortium Project (2021H003), and the Henan Province Major Science and Technology Project (221100210300).

  2. Author contributions: Yanmin Zhang: writing – review and editing. Baohuan Huang: writing – original draft. Hongjiao Gao: writing – review and editing. Shanguang LI: visualization. Fei Zhou: visualization. Kexing Song: writing – review and editing. All authors have accepted responsibility for the entire content of this manuscript and approved its submission.

  3. Conflict of interest: The authors state no conflict of interest.

  4. Data availability statement: The datasets generated and/or analyzed during the current study are available from the corresponding author on reasonable request.

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Received: 2024-04-09
Revised: 2024-06-15
Accepted: 2024-07-14
Published Online: 2024-08-29

© 2024 the author(s), published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 International License.

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  3. Polyvinylpyrrolidone-stabilised gold nanoparticle coatings inhibit blood protein adsorption
  4. Energy and mass transmission through hybrid nanofluid flow passing over a spinning sphere with magnetic effect and heat source/sink
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  10. Dual numerical solutions of Casson SA–hybrid nanofluid toward a stagnation point flow over stretching/shrinking cylinder
  11. Single flake homo p–n diode of MoTe2 enabled by oxygen plasma doping
  12. Electrostatic self-assembly effect of Fe3O4 nanoparticles on performance of carbon nanotubes in cement-based materials
  13. Multi-scale alignment to buried atom-scale devices using Kelvin probe force microscopy
  14. Antibacterial, mechanical, and dielectric properties of hydroxyapatite cordierite/zirconia porous nanocomposites for use in bone tissue engineering applications
  15. Time-dependent Darcy–Forchheimer flow of Casson hybrid nanofluid comprising the CNTs through a Riga plate with nonlinear thermal radiation and viscous dissipation
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https://doi.org/10.1515/ntrev-2024-0075
Keywords for this article
C19400 alloy; bending performance; dislocation density
Creative Commons
BY 4.0

Articles in the same Issue

  1. Research Articles
  2. Tension buckling and postbuckling of nanocomposite laminated plates with in-plane negative Poisson’s ratio
  3. Polyvinylpyrrolidone-stabilised gold nanoparticle coatings inhibit blood protein adsorption
  4. Energy and mass transmission through hybrid nanofluid flow passing over a spinning sphere with magnetic effect and heat source/sink
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  112. A review on strengthening mechanisms of carbon quantum dots-reinforced Cu-matrix nanocomposites
  113. Review on nanocellulose composites and CNFs assembled microfiber toward automotive applications
  114. Nanomaterial coating for layered lithium rich transition metal oxide cathode for lithium-ion battery
  115. Application of AgNPs in biomedicine: An overview and current trends
  116. Nanobiotechnology and microbial influence on cold adaptation in plants
  117. Hepatotoxicity of nanomaterials: From mechanism to therapeutic strategy
  118. Applications of micro-nanobubble and its influence on concrete properties: An in-depth review
  119. A comprehensive systematic literature review of ML in nanotechnology for sustainable development
  120. Exploiting the nanotechnological approaches for traditional Chinese medicine in childhood rhinitis: A review of future perspectives
  121. Twisto-photonics in two-dimensional materials: A comprehensive review
  122. Current advances of anticancer drugs based on solubilization technology
  123. Recent process of using nanoparticles in the T cell-based immunometabolic therapy
  124. Future prospects of gold nanoclusters in hydrogen storage systems and sustainable environmental treatment applications
  125. Preparation, types, and applications of one- and two-dimensional nanochannels and their transport properties for water and ions
  126. Microstructural, mechanical, and corrosion characteristics of Mg–Gd–x systems: A review of recent advancements
  127. Functionalized nanostructures and targeted delivery systems with a focus on plant-derived natural agents for COVID-19 therapy: A review and outlook
  128. Mapping evolution and trends of cell membrane-coated nanoparticles: A bibliometric analysis and scoping review
  129. Nanoparticles and their application in the diagnosis of hepatocellular carcinoma
  130. In situ growth of carbon nanotubes on fly ash substrates
  131. Structural performance of boards through nanoparticle reinforcement: An advance review
  132. Reinforcing mechanisms review of the graphene oxide on cement composites
  133. Seed regeneration aided by nanomaterials in a climate change scenario: A comprehensive review
  134. Surface-engineered quantum dot nanocomposites for neurodegenerative disorder remediation and avenue for neuroimaging
  135. Graphitic carbon nitride hybrid thin films for energy conversion: A mini-review on defect activation with different materials
  136. Nanoparticles and the treatment of hepatocellular carcinoma
  137. Special Issue on Advanced Nanomaterials and Composites for Energy Conversion and Storage - Part II
  138. Highly safe lithium vanadium oxide anode for fast-charging dendrite-free lithium-ion batteries
  139. Recent progress in nanomaterials of battery energy storage: A patent landscape analysis, technology updates, and future prospects
  140. Special Issue on Advanced Nanomaterials for Carbon Capture, Environment and Utilization for Energy Sustainability - Part II
  141. Calcium-, magnesium-, and yttrium-doped lithium nickel phosphate nanomaterials as high-performance catalysts for electrochemical water oxidation reaction
  142. Low alkaline vegetation concrete with silica fume and nano-fly ash composites to improve the planting properties and soil ecology
  143. Mesoporous silica-grafted deep eutectic solvent-based mixed matrix membranes for wastewater treatment: Synthesis and emerging pollutant removal performance
  144. Electrochemically prepared ultrathin two-dimensional graphitic nanosheets as cathodes for advanced Zn-based energy storage devices
  145. Enhanced catalytic degradation of amoxicillin by phyto-mediated synthesised ZnO NPs and ZnO-rGO hybrid nanocomposite: Assessment of antioxidant activity, adsorption, and thermodynamic analysis
  146. Incorporating GO in PI matrix to advance nanocomposite coating: An enhancing strategy to prevent corrosion
  147. Synthesis, characterization, thermal stability, and application of microporous hyper cross-linked polyphosphazenes with naphthylamine group for CO2 uptake
  148. Engineering in ceramic albite morphology by the addition of additives: Carbon nanotubes and graphene oxide for energy applications
  149. Nanoscale synergy: Optimizing energy storage with SnO2 quantum dots on ZnO hexagonal prisms for advanced supercapacitors
  150. Aging assessment of silicone rubber materials under corona discharge accompanied by humidity and UV radiation
  151. Tuning structural and electrical properties of Co-precipitated and Cu-incorporated nickel ferrite for energy applications
  152. Sodium alginate-supported AgSr nanoparticles for catalytic degradation of malachite green and methyl orange in aqueous medium
  153. An environmentally greener and reusability approach for bioenergy production using Mallotus philippensis (Kamala) seed oil feedstock via phytonanotechnology
  154. Micro-/nano-alumina trihydrate and -magnesium hydroxide fillers in RTV-SR composites under electrical and environmental stresses
  155. Mechanism exploration of ion-implanted epoxy on surface trap distribution: An approach to augment the vacuum flashover voltages
  156. Nanoscale engineering of semiconductor photocatalysts boosting charge separation for solar-driven H2 production: Recent advances and future perspective
  157. Excellent catalytic performance over reduced graphene-boosted novel nanoparticles for oxidative desulfurization of fuel oil
  158. Special Issue on Advances in Nanotechnology for Agriculture
  159. Deciphering the synergistic potential of mycogenic zinc oxide nanoparticles and bio-slurry formulation on phenology and physiology of Vigna radiata
  160. Nanomaterials: Cross-disciplinary applications in ornamental plants
  161. Special Issue on Catechol Based Nano and Microstructures
  162. Polydopamine films: Versatile but interface-dependent coatings
  163. In vitro anticancer activity of melanin-like nanoparticles for multimodal therapy of glioblastoma
  164. Poly-3,4-dihydroxybenzylidenhydrazine, a different analogue of polydopamine
  165. Chirality and self-assembly of structures derived from optically active 1,2-diaminocyclohexane and catecholamines
  166. Advancing resource sustainability with green photothermal materials: Insights from organic waste-derived and bioderived sources
  167. Bioinspired neuromelanin-like Pt(iv) polymeric nanoparticles for cancer treatment
  168. Special Issue on Implementing Nanotechnology for Smart Healthcare System
  169. Intelligent explainable optical sensing on Internet of nanorobots for disease detection
  170. Special Issue on Green Mono, Bi and Tri Metallic Nanoparticles for Biological and Environmental Applications
  171. Tracking success of interaction of green-synthesized Carbopol nanoemulgel (neomycin-decorated Ag/ZnO nanocomposite) with wound-based MDR bacteria
  172. Green synthesis of copper oxide nanoparticles using genus Inula and evaluation of biological therapeutics and environmental applications
  173. Biogenic fabrication and multifunctional therapeutic applications of silver nanoparticles synthesized from rose petal extract
  174. Metal oxides on the frontlines: Antimicrobial activity in plant-derived biometallic nanoparticles
  175. Controlling pore size during the synthesis of hydroxyapatite nanoparticles using CTAB by the sol–gel hydrothermal method and their biological activities
  176. Special Issue on State-of-Art Advanced Nanotechnology for Healthcare
  177. Applications of nanomedicine-integrated phototherapeutic agents in cancer theranostics: A comprehensive review of the current state of research
  178. Smart bionanomaterials for treatment and diagnosis of inflammatory bowel disease
  179. Beyond conventional therapy: Synthesis of multifunctional nanoparticles for rheumatoid arthritis therapy
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