Surface Properties and Corrosion Behavior of Turn-Assisted Deep-Cold-Rolled AISI 4140 Steel

In this research, the effect of various turn-assisted deep-cold-rolling process parameters on the residual stress, microstructure, surface hardness, surface finish, and corrosion behavior of AISI 4140 steel has been investigated. The examination of the surface morphology of the turned and processed samples was performed by using a scanning electron microscope, energy-dispersive spectroscopy, and atomic force microscopy. Response surface methodology and desirability function approach were used for reducing the number of experiments and finding local optimized conditions for parameters under the study. The results from the residual stress measurements indicate that the rolling force has the highest effect by generating a deeper layer of residual compressive stress. The outcomes of surface hardness and surface finish emphasize that rolling force and number of tool passes are the most significant parameters affecting the responses. Surface studies confirmed the corrosion and its intensity onto the metal surface, and according to atomic force microscopy studies, the surface had become remarkably rough after exposure to the corrosive medium. Improvements in surface microhardness from 225 to 305.8 HV, the surface finish from 4.84 down to 0.261 μm, and corrosion rate from 6.672 down to 3.516 mpy are observed for a specific set of parameters by turn-assisted deep-cold-rolling process. The multiresponse optimization for surface finish and corrosion rate together shows that a ball diameter of 10 mm, a rolling force of 325.75 N, initial roughness of 4.84 µm, and number of tool passes of 3 give better values for the two responses under consideration with composite desirability of 0.9939. Based on the experimental work at the optimum parameter setting, the absolute average error between the experimental and predicted values for the corrosion rate is calculated as 3.2%.


Introduction
Most of the components used in the aerospace and automobile industry require excellent surface characteristics as they work under severe conditions (Ref 1). Fatigue is one of the main reasons for the failure of these components. About 90% of all mechanical service failures are due to fatigue ( Ref 2,3). The fatigue failure relies entirely upon the ultimate strength or yield stress of the material. But actuality, different factors, for example, geometry, quality of the surface, type of material, residual stresses, loading direction, size of the grain, surrounding atmosphere, operating temperature may reduce the service life of a component ( Ref 4,5). Fatigue occurs due to cracks originated on free surfaces, and therefore fatigue life is reliant on the surface finish (Ref [6][7][8]. Residual compressive stress on the surface and near surface of a part is beneficial as it enhances the fatigue life by slowing down the rate of crack propagation (Ref 9,10). Tensile residual stress on the surface of the component is generally detrimental as it decreases the fatigue life by speeding the rate of crack propagation and lowering the resistance to environmentally assisted cracking ( Ref 11,12). Generally, turning results in tensile residual stress, which is not beneficial for fatigue life. Hence, secondary processes are adopted to improve fatigue life. In addition to the failure due to fatigue, corrosion of machine components results in significant financial losses and may also be responsible for acute and costly breakdowns ( Ref 13). Due to the enormous loss, the problems related to corrosion need to be considered seriously. Effective protective techniques need to be applied to reduce corrosion. Some of the methods to prevent corrosion are using metals and alloys having excellent resistance to corrosion, protective coating, passive layers, surface finishing operations, etc.
The corrosion of high-strength steel and its association with surface morphology have been a concern for product sustainability. This is due to the layer of chromium oxide on the metal surface preventing corrosion. The data related to the association between the surface morphology and corrosion behavior of stainless steel can be found in the literature ( Ref 14). The surface morphology of a metal constituent is determined by surface finishing processes that affect the corrosion. In specific, the surfaces prepared by mechanical processes are greatly affected by the wear processes. Different surface textures are obtained with different wear modes resulting in different surface finishes. To explain the exclusive features of the surfaces, several roughness parameters have been established, and among them, the root-mean-square average roughness (R q ) and the average surface roughness (R a ) are the most commonly used parameters ( Ref 14).
Components used in the present day ask for materials with superior surface characteristics such as high resistance to corrosion and wear, improved surface hardness and finish, residual stress ( Ref 15). Using alloys will increase the cost of the components; hence, few mechanical surface enhancement (MSE) methods are utilized. The MSE methods such as shot peening, laser shock peening, burnishing will impart the compressive residual stress near the surface and will enhance the surface properties such as wear resistance, residual compressive stress, corrosion resistance, surface hardness and finish ( Ref 11,12,[16][17][18][19]. However, the methods revealed above, except burnishing, always produce rough surface and would remove the advantageous impacts of a surface nanocrystalline microstructure ( Ref 15). Enormous roughness may promote stress concentration at specific sites and hence initiate crack, particularly under fatigue loading conditions ( Ref 20). Hence, decreasing the surface roughness is as important as surface nanocrystallization on improving the materialÕs performance, including corrosion resistance (Ref 21). One of the MSE methods, deep cold rolling (DCR), is getting attention nowadays as it is a fast, chipless, and economical surface enhancement method applicable to prevailing conventional or computer numerical control (CNC) machine tools. Further producing a deep layer of compression and nanocrystalline microstructure on the surface of samples, it also can lessen the surface roughness of materials and enhance the fatigue life of engineering components without affecting their bulk properties (Ref [22][23][24][25][26][27][28][29][30][31][32][33][34]. There are numerous parameters to be considered, and the effects of each of these parameters are dependent on other variables. In addition to the experimental studies, predictive models are necessary to understand further the mechanisms that drive the surface integrity changes and to discover the optimum machining settings that would lead to desirable surface integrity ( Ref 35). So, the design of experiments (DOE) is utilized where the effect of various process parameters can be studied simultaneously with these proficient structures, rather than in a trial-and-error approach, giving truly reproducible outcomes ( Ref 26,[36][37][38][39]. Response surface methodology (RSM) is a mixture of numerical and measurable strategies for the experimental model structure. Via a cautious plan of trials, the goal is to optimize a response/s, which is affected by various factors (Ref [40][41][42][43]. AISI 4140 steel possesses excellent mechanical properties and is often used as axle/crankshaft material in automobile industries. Cracking of this part will seriously affect the safety of the vehicles. Y.X. Zhao et al. (Ref 44) studied short fatigue crack propagation and found that effective microcracks initiated from the ferrite on the surfaces of the material. Therefore, improving the surface properties of machine components that work under fatigue and corrosion is an effective way to enhance the service life of the components. Although surface alteration by application of the deep-cold-rolling process is quite new, it has received substantial demand due to enhanced residual compressive stress ( Ref 29,45) , surface work hardening ( Ref 28,46) , surface finish ( Ref 18,47) and grain refinement which in turn will have the positive effect on corrosion properties. Therefore, a surface enhancement method improving the surface properties after the machining would be beneficial along with the effective use of the design of experiment to reduce the time and number of experiments to be conducted. Based on the above literature analysis, it is clear that the effects of deep-cold-rolling process parameters on the surface integrity of titanium alloys, magnesium alloys, and hardened steel have been explored ( Ref 4,23,28,34,45,48,49). However, the literature on the effects of various deep rolling parameters on the surface integrity of AISI 4140 steel is limited ( Ref 49,50). A survey in the literature also indicates that there are few investigations about the application of DOE methods for optimizing the process parameters for enhanced surface characteristics ( Ref 4,51).
Therefore, this study has been focused on achieving the enhanced surface properties (residual stress, surface hardness, surface finish, and corrosion behavior) of AISI 4140 steel through a custom-made turn-assisted deep-cold-rolling (TADCR) tool and setup and optimizing the various process parameters (ball diameter, rolling force, initial roughness of the workpiece, and number of tool passes) for better responses by using response surface methodology and desirability function approach. The corrosion behavior of AISI 4140 steel for the turned and turn-assisted deep-cold-rolled samples was made to undergo a weight loss (gravimetric analysis) technique for corrosion rate measurement in 3.5% NaCl solution. Scanning electron microscope (SEM) and energy-dispersive spectroscopy (EDS) analyses were used for surface morphology studies and elemental analysis of the surface layers, respectively. The atomic force microscopy (AFM) analysis was carried out to reveal the relation between corrosion rate and average surface roughness (R a ).

Material and Experimental Setup
The study conducted on AISI 4140 steel contains nickel, chromium, and molybdenum, which increases its passivation and consequently enhances resistance to corrosion. Thus, this is a suitable steel to be used in an aggressive medium. It finds vast application in automobile and aerospace industry for the manufacture of various parts experiencing fatigue loads (Ref 52,53). The primary chemical ingredients of the material used in wt% are as follows: C-0.40, Si-0.27, Mn-0.66, Cr-1.20, Mo-0.25, Ni-0.16, Cu-0.12. The mechanical properties of the as-bought material are as follows: yield strength-850 MPa, ultimate tensile strength-949 MPa, Vickers hardness-225 VHN. Specimens are first turned to the required diameter to render similar surface roughness. The detailed view of the experimental setup retrofitted on the lathe is given in Fig. 1. Four-component Kistler dynamometer of type 9272A was used for the measurement of forces while TADCR is attached on the cross slide of the lathe. The force values were recorded in a laptop through DynoWare force measuring software. To restrict the bending of the specimen at a higher rolling force, a follower rest/backrest mechanism was provided. Here, the sample will have support from the back as well as from the top with rolling contact elements as shown in Fig. 1 to reduce bending of the specimen and friction. To ensure a point of contact between the follower rest and the specimen, tungsten carbide balls were provided.

CCD Experiments
Four process factors as shown in Table 1 are identified to have a significant effect on the TADCR process. These process parameters are chosen at three levels. During the experiments, apart from these parameters, the remaining three parameters are set at favorable values identified from screening experiments (i.e., ball material-tungsten carbide, feed rate-36 mm/min and lubricant oil-brake oil). The scheme of central composite design (CCD) adopted with three levels of each parameter is shown in Table 1.

Response Characterization Methods
Residual stresses (RS) imparted due to TADCR are measured using Rigaku x-ray residual stress analyzer. Residual stress was measured at different depths of 0.05, 0.1, 0.2, 0.3, 0.4, and 0.5 mm from the workpiece surface. Surface hardness (SH) of samples was measured with the help of Matsuzawa Micro Vickers hardness tester. The Vickers indentor loaded with 4.905 N for a loading period of 10 s is used to evaluate microhardness variations with increments of 25 lm between two successive indentations. The surface of the specimen was examined using different characterization techniques. Microstructure examination of the test surface was done before and after the TADCR process by utilizing optical microscopy.
A Taylor Hobson Surtronic 3+ surface measuring instrument was used to discover the surface structure and surface finish at a microscale. An IB342 Innova model atomic force microscopy (AFM) was utilized to measure the surface finish and surface structure in nanoscale. The corrosion rate (CR) of the samples before and after TADCR at a various combination of parameters is calculated by using the weight loss (WL) method. The surface is checked through a JEOL JSM-6380L analytical scanning electron microscope (SEM) connected with the   energy-dispersive x-ray (EDX) to examine the surface morphology and to evaluate the elements on the surface of the specimen before and after immersing in the corrosive medium.

Corrosion Investigations using the Weight Loss Method
The weight loss experiments were performed on cylindrical specimens having the dimensions 9.48 mm diameter and 10 mm length. Turned and deep-cold-rolled specimens at various parameter settings were dipped in 100-mL glass beakers comprising 60 mL 3.5% NaCl solution for immersion time of 936 h at room temperature (30 ± 1°C). To identify the specimens dipped in the corrosive medium, numbered labels were pasted on each beaker. Before taking all the readings, the surface exposed to the corrosive medium is thoroughly washed with double distilled water, degreased and dried with acetone. Before measurement, the samples were kept in a desiccator over a silica gel for 24 h. The corrosion product layer is scratched off with a fiber brush and promptly drenched in the pickling arrangement containing concentrated nitric acid (86%) for 5 min (ASTM G1). Once all the corrosion products were completely removed from the surface, the samples were flushed with deionized water and ethanol, dried with a surge of air, and weighed again to decide weight reduction. Duplicate tests were conducted for all the weight loss tests. The variance between the initial and final weights of the sample is used to determine the CR. The corrosion rate (in mpy) is calculated by using the following formula (54): CR ¼ KW ATD , where K is a constant (3.45 9 10 6 ), W is the difference between the initial and final weights of the sample in gms, D is the density of the sample in g/cm 3 , A is the area of the sample exposed to corrosive medium in cm 2 , and T is the immersion time in hours.

Residual Stress Analysis
Residual stress in specimens treated with the TADCR process is given in Table 2. The compressive residual stress of TADCR specimens is far higher when compared with the untreated/turned specimen. This increase is because of the cold working proven as elongation of grains. Figure 2 shows a considerable amount of residual compressive stresses at the surface and near-surface area after the TADCR process. Maximum residual compressive stress measured experimentally is 569 MPa immediately below the surface rolled at 750 N force. This is significantly more compared to residual stress in the turned sample measured at + 94 MPa (tensile). The maximum residual compressive stress of 293 MPa is seen in the sample deep cold rolled at a lower force of 250 N. From Fig. 2, it is also noticed that the penetration of compressive residual stress layer for TADCR with 750 N is 0.3 mm and 250 N rolling force is 0.1 mm. Thus, 750 N rolling force induces the compression layer to a depth nearly three times greater than at 250 N rolling force. This could be seen manifested as grain elongation in microstructure, as explained below.
The microstructure of the unrolled (as-turned) specimen shown in Fig. 3a shows equiaxial proeutectoid ferrite grains with pearlitic phases. The white patches show the proeutectoid ferritic phases with large colonies of pearlitic (light area) regions. The microstructure remains the same from the surface toward the core of the specimen. The microstructure of the TADCR specimen operated with 750 N rolling force displays elongated grains, as shown in Fig. 3c. Here, the deformation and elongation of grain in the direction of rolling can be seen. The intensity of elongation is more near the surface where the tool is in contact with the workpiece, and also, deeper penetration is observed. As the depth increases, the grain elongation intensity reduces. The farthest region from the surface seems to be unaffected by the deep-coldrolling process. Figure 3b shows the microstructure of the TADCR specimen, where the process was done with the rolling force of 250 N, which is much less than the previous case. From  Fig. 3b, it is seen that the grains are partially elongated to a depth of around 0.1 mm from the surface. The reason is that the force applied on the workpiece surface is mostly utilized to level the peaks and valleys. Thus, the generated residual compressive stress is very less as compared to the previous condition. From this, we can conclude that the rolling force has a significant effect on the generation of residual compressive stress on the surface. The higher the rolling force, the deeper will be the layer of residual compressive stress generated. Similar results can also be seen from the residual stress analysis shown in Fig. 2.

Surface Hardness
The average values of surface hardness with different process parameters are recorded in Table 3. From the analysis, the rolling force has the highest effect on the surface hardness, followed by ball diameter with a contribution of 66.22 and 16.29%, respectively. Hardness at the surface and near surface increases with an increase in ball diameter, rolling force, and the number of passes and decreases with an increase in the initial roughness of the workpiece.
The subsurface microhardness found at various depths of the specimen is shown in Fig. 4. The nature of the curve obtained for microhardness of TADCR samples concerning the depth at different rolling forces is almost similar. The highest hardness is observed at the surface, then gradually decreases, and reaches the value of the turned sample. The average microhardness of the turned specimen on the surface is around 225 HV. Maximum hardness of about 306 HV is recorded on the surface for TADCR with a force of 750 N, and the hardness is found to decrease when we go deep from the surface and ultimately settle down at hardness of turned sample at a depth of about 300 lm. It could also be observed that surface microhardness settles at a depth of 175 and 100 lm for TADCR with 500 and 250 N force, respectively. This variation  complements the variation in residual stress shown in Fig. 2.
Higher hardness at the surface logically diminishing is because of the differential measure of cold work experienced by the material.

Surface Finish
Surface finish values after TADCR with various factors are recorded and given in Table 3. The results indicate that the number of tool passes and ball diameter are the two most significant factors affecting the surface finish with 68.22 and 10.35% contributions, respectively. The surface finish increases with the increase in the ball diameter and number of tool passes and decreases with the increase in rolling force and initial roughness of the workpiece. One of the roughness profiles of the turned specimen is shown in Fig. 5a. A higher value of R a is observed because the deviation from the mean line is significant. Similarly, Fig. 5b shows the roughness profile of the TADCR sample, where we have observed lower R a value (the deviation from the mean line is small), suggesting improvement in surface finish.

Corrosion Rate Measurement from Weight Loss Method
The corrosion rate measurement is done by using the weight loss method for the TADCR specimens operated with various process parameter settings, which is summarized in Table 3. The relative effect of each process parameter on the corrosion rate is presented in the analysis of variance (ANOVA) in Table 4. The results of ANOVA indicate that ball diameter has the greatest influence on the corrosion rate with a 33% contribution followed by the interaction effect of rolling force and initial roughness of the workpiece with a 29% contribution. The rate of corrosion increases with a decrease in ball diameter, an increase in rolling force, initial roughness of the workpiece, and number of tool passes, as displayed in the main effect plot shown in Fig. 6. The ''fitted means'' interaction plot depends on the thought ''smaller the better'' for the corrosion rate. In the interaction plot, if there exists an interaction between the factors at certain levels, they are represented by crossed lines. Straight, parallel lines represent no evidence of an interaction between the factors. From Fig. 7, it is noted that significant interaction exists between the rolling force and the initial roughness of the workpiece. The parameters S, R 2 , and adjusted R 2 measure how well the model fits the data. The values of S, R 2 , and adjusted R 2 will assist in choosing the model with the best fit when comparing various models for the examination. The smaller value of S indicates that the model better forecasts the response.   Table 4, R 2 ðadjÞ is relatively close to 1 (Table 5).
An empirical model is developed from the principles of response surface methodology for the corrosion rate. The predicted values from the empirical model are compared with the experimentally measured values. Based on the empirical model developed for the response, the contour plots are drawn to visualize the effect of process parameters. An empirical model is developed for the corrosion rate based on experimental values and is given as Eq 1. The model acquired was used to foresee the response for all values of variables inside the cutoff points considered. The model is satisfactory at a 95% certainty level. At the point when P values are under 0.05, the acquired models are viewed as measurably noteworthy. It exhibits that the terms picked in the model have substantial effects on the responses: CR ¼ À3:545 þ 0:928X 1 þ 0:002164X 2 þ 1:293X 3 þ 0:372X 4 À 0:08642X 2 1 þ 0:000002X 2 2 À 0:1040X 2 3 À 0:0103X 2 4 þ 0:000016X 1 X 2 þ 0:05597X 1 X 3 À 0:00574X 1 X 4 À 0:000693X 2 X 3 À 0:000025X 2 X 4 À 0:0563X 3 X 4 ðEq 1Þ At a 95% confidence level, a close match is observed between the predicted and experimentally obtained values, as shown in Fig. 8. It shows that the residuals fall on a straight line suggesting that the errors are distributed normally, and the maximum average error is found to be only about 1.68% between the experimental and predicted values. From Fig. 9, it is seen that the alteration in the size of the ball influences the corrosion rate. The large contact area of the larger diameter ball enters the surface to a smaller depth than a small-diameter ball under definite rolling force. From Fig. 9, it is also revealed that by increasing the ball diameter and rolling force, the rate of corrosion decreases. The increase in the pressure of ball during the TADCR process on the workpiece surface squeezes most of the asperities and increases the flow of metal on the surface. This leads to the filling of more peaks and/ or valleys that existed on the subsurface due to turning. As the surface finish is enhanced, the area of the surface, which comes into contact with the corrosive medium, decreases, and thus decrease in corrosion rate is observed. Further increase in rolling force will diminish the surface finish because expanding the rolling force past a specific value disintegrates the surface finish on account of over solidifying and hence chipping of the surface layers. This is the reason behind increase in corrosion rate at higher rolling force. A blend of larger ball diameter with lesser rolling force, low initial roughness, and more number of tool passes will lead to a considerable reduction in corrosion rate, as shown in the response optimization plot (Fig. 10). The outcomes show that the ball diameter is one of the most critical variables influencing the corrosion rate. It tends to be seen that larger ball diameter with lower initial roughness of the workpiece resulted in a lesser corrosion rate. It is observed that the mix between more number of tool passes and larger ball diameter and lower rolling force with lower initial roughness of the workpiece brings about an extensive improvement in the corrosion rate. The optimum TADCR parameters for achieving lower corrosion rates are determined as ball diameter of 10 mm, rolling force of 250 N, initial roughness of 4.84 lm, and number of passes of 3.

Multiresponse Optimization of TADCR Process Variables
The desirability function approach (DFA) is one of the most widely used methods for the optimization of multiple response processes. It is based on the idea that the ''quality'' of a product or process that has multiple quality characteristics, with one of them outside of some ''desired'' limits, is entirely unacceptable. The method finds operating conditions that provide the ''most desirable'' response values. Figure 11 shows the multiresponse optimization plot for surface finish and corrosion rates together obtained from the desirability function approach. It is a mathematical process to discover the optimal values of input parameters and multiple responses concurrently by using the optimum input parameter levels. Both surface finish and corrosion rates have been allotted a target value, as given in Table 6. Here, the aim is to achieve an excellent surface finish with a lower corrosion rate. In the multiresponse optimization plot, the main effect plots of surface finish and corrosion rate with desirability (d) are given separately. Along with this, composite desirability (D) is also provided. The use of composite desirability is to evaluate how well the settings optimize a set of responses (surface finish and corrosion rate) overall. Desirability has a range of zero to one. One represents the ideal case; zero indicates that one or more responses are outside their acceptable limits. Composite desirability is the weighted geometric mean of the individual desirabilities for the responses.   Figure 11 shows the multiresponse optimization plot for surface finish and corrosion rates together. From Fig. 11, it can be found that a ball diameter of 10 mm, a rolling force of 325.75 N, initial roughness of 4.84 lm, and number of passes of 3 give better values for the two responses under consideration with composite desirability of 0.9939.
3.5.1 Confirmation Experiments Performed at Optimum Parameter Setting. A set of validation experiments was performed at optimal parameter settings to confirm the enhancement made to performance characteristics. The purpose of validation trials is to verify the repetitiveness of the investigated results and validate the accuracy of the predictive model. TADCR process parameters are set at optimum levels as determined from DFA and response surfaces, as depicted in Table 7.
The results from the confirmation experiments of the corrosion rate obtained at optimum process parameters are shown in Table 8. From the results, it is observed that the predicted results are in agreement with experimental test results. Based on the experimental work at the optimum parameter setting, the absolute average error between the

Surface Morphology Studies
Once the optimum process parameters were identified for TADCR, in order to study the surface morphology, SEM and AFM analysis was carried out. For the SEM and AFM analysis, only three samples were selected (TADCR sample, TADCR sample where the lowest corrosion rate was observed, and TADCR sample where the highest corrosion rate was observed) out of the 31 samples.

SEM and Energy-Dispersive Spectroscopy (EDS)
Analysis. SEM images of the AISI 4140 TADCR steel sample (Fig. 12a) and the TADCR samples for the experimental run order 6 and 23 (refer Table 3) where the lowest and highest corrosion rates were observed (Fig. 12b and c) during the experiments with 3.5% NaCl solution as the corrosive medium immersed for a duration of 936 h were taken for the analysis. The TADCR sample did not display any evident flaws, excluding a few nanosize abrasions, as shown in Fig. 12(a). When the surface of deep-cold-rolled AISI 4140 steel sample was observed in higher magnification in contact  3.5% NaCl for 936 h, its surface seems to be rough, as shown in (b) and (c). It is detected that the surface of sample no. 23 had lesser roughness compared to sample no. 06 which is attributed to less corrosion and higher corrosion resistance. SEM analysis confirmed the corrosion and its intensity of corrosion on the metal surface.
The EDS was analyzed for the TADCR AISI 4140 steel sample before corrosion and after corrosion with a 3.5% NaCl solution and is shown in Fig. 13. The data of the elemental analysis are also given in the same figure. The surface atomic composition before corrosion confirms the surface composition of the metal sample. In general, the Fe percentage decreased after immersion in 3.5% NaCl solution and oxygen percentage increased. After the corrosion process, there is a presence of Na and Cl atoms in EDS, confirming the corrosion process of metal with NaCl due to the dissolution of a metal layer.
3.6.2 AFM Analysis. The 3D AFM method is one of the methodologies for investigating the surface topography at the nano-and microlevels. The optical profilometry provides qualitative images at the microscale level. The AFM images of TADCR AISI 4140 steel are given in Fig. 14 for samples 6 and 23. The samples are exposed to 3.5% NaCl which is taken after exposure for 936 h, and AFM analysis was done on the surface. Surface roughness of samples 6 and 23 when in contact with 3.5% NaCl has increased when compared to the TADCR sample without immersion. The increase in roughness can be attributed to the higher corrosion tendency of sample no. 6 when compared to sample no. 23. The R a values show that the roughness of the material immersed in 3.5% NaCl solution for the TADCR sample no. 6 increases to 304 nm from 40.3 nm and for the TADCR sample no. 23 increases to 186 nm from 27 nm. From the AFM analysis, it is also revealed that the corrosion rate is directly proportional to the R a value. AISI 4140 steel sample operated with a ball of 10 mm diameter and 250 N rolling force resulted in lower R a value when compared to the sample operated with a ball of 6 mm diameter and 750 N rolling force.

Conclusions
Stringent demands in modern manufacturing have created the need to produce parts that have a better finish, high corrosion resistance, and service life. The research is aimed at studying the influence of process variables on surface enhancement and corrosion rate of TADCR of AISI 4140 steel. DOE is used to investigate and analyze the effects systematically. Study with CCD and RSM used to evaluate the surface hardness, surface finish, and corrosion rate results in the following conclusions: • The results from the experiment depict that compared to the untreated samples, deep cold rolling significantly enhanced the surface hardness, to a maximum (306 HV), which then reaches the bulk hardness (225 HV) measured toward the core of the specimen. The rolling force and ball diameter play an essential role in improving the surface hardness of TADCR specimens with a contribution of 66.22 and 16.29%. The number of tool passes and ball diameter are the two most significant parameters playing the primary role in enhancing the surface finish with 68.22 and 10.35% contributions respectively. • The ball diameter plays a significant role in reducing the corrosion rate of TADCR specimens with a 33% contribution followed by the interaction effect of rolling force and initial roughness of the workpiece with a 29% contribution. The improved corrosion resistance of the TADCR sample is due to the refinement of grains, higher surface hardness, and residual compressive stress. • The study revealed a significant compressive stress layer up to 300 lm below the surface with a rolling force of 750 N. The study also revealed one-to-one correlations between the rolling force, increase in microhardness, the magnitude of residual compressive stresses. Confirmation experiments were conducted with the opti-mum parameter setting to validate the improvements in response, and it is observed that the deviation between optimum predicted and confirmatory experimental values is about 5%. • SEM and AFM analysis shows a relatively smooth surface of the AISI 4140 steel sample processed with a deep-coldrolling technique operated with a 10-mm-diameter ball and 250 N rolling force.

Funding
Open access funding provided by Manipal Academy of Higher Education, Manipal.

Open Access
This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing, adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons licence, and indicate if changes were made. The images or other third party material in this article are included in the article's Creative Commons licence, unless indicated otherwise in a credit line to the material. If material is not included in the article's Creative Commons licence TADCR sample no. 6 + 3.5% NaCl and (c) TADCR sample no. 23 + 3.5% NaCl and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this licence, visit http://creativecommons.org/licenses/by/4.0/.