Strojniški vestnik - Journal of Mechanical Engineering 67(2021)1-2, 45-52, © 2021 Journal of Mechanical Engineering. All rights reserved.
D0l:10.5545/sv-jme.2020.6912	Original Scientific Paper
Received for review: 2020-08-27 Received revised form: 2020-12-16 Accepted for publication: 2021-01-14
An Investigation on Laser Welding Parameters on the Strength of TRIP Steel
Khot Rahul S1 - T. Venkateshwara Rao2 - Harshad Natu3 -H.N. Girish4 - Tadashi Ishigaki5 - Puttaswamy Madhusudan67* 1 K L University, Mechanical Department, India 2 DBS Institute of Technology, Mechanical Department, India
3 Magod Fusion Laser Welding System, India 4 University of Mysore, Department of Earth Science, India 5 Tottori University, Faculty of Engineering, Japan 6 Environmental Engineering and Management Research Group, Ton Duc Thang University, Ho Chi Minh City, Vietnam 7 Faculty of Environment and Labour Safety, Ton Duc Thang University, Ho Chi Minh City, Vietnam
The energy required for joining steel segments by using laser welding is relatively very low compared with arc welding, gas welding, or any other conventional welding techniques. Moreover, the rapid cooling may create a significant effect on different regions, such as the fusion zone (FZ), heat affected zone (HAZ), and base metal (BM), and in turn affect different parameters. In this study, the characteristics of the laser-welded joint were investigated by varying laser power, welding velocity and incident angle, and tensile strength. In our, experiments. the microhardness was increased by varying the power of laser welding. The strength of the joint was increased to 549 MPa with 2200 W high power, 30 mm/s velocity, and 80° laser incident angle. By increasing the power and velocity of the laser, the welding gun strength was improved; conversely, the angle of laser incident on the welding location decreased while its strength was increased. Keywords: TRIP steel, laser welding, Nd:YAG laser, mechanical strength, microhardness
Highlights
•	The effect of laser power, laser welding velocity, and incident angle were examined, which revealed enhanced mechanical properties.
•	Microhardness was increased to 549 MPa by increasing the power of laser welding.
•	Welding strength is improved by varying the power and velocity.
•	Varying the laser incident angle 9.62 % tensile strength and 67 % deformation was achieved.
0 INTRODUCTION
Throughout the world fuel consumption is significantly increasing day by day, so to meet the increasing demand, energy costs have been considerably increasing [1] to [3]. In this regard, to reduce fuel consumption, automobile industries are considering cutting down the weight of vehicles to improve their overall performance and fuel economy [4] to [6]. The continuous development in new grades of steel from global steel industries, with the required features and ever-increasing strength, has remarkably improved the demand for advanced high-strength steels (AHSS) in the market [7]. The AHSS are complicated materials with precise chemical content and different phase, resulting from accurately restrained heating and cooling mechanisms [8] and [9]. Recently, a variety of strengthening methods have been developed to enhance the strength, flexibility, persistence, and lethargy properties in steel [10]. However, at present, tensile strengths as short of 440 MPa, are observed in several AHSS phases and hence, there is a need to utilize force as a threshold to enhance the AHSS
steel. At present, it is recommended that an additional constituent of the family of AHSS-termed dual-phase (DP) steel is delicate at the sub-critical heat-damaged zone due to restraining of the martensite [11] to [18].
Furthermore, the transformation induced plasticity (TRIP) steels with enormous strength and ductility properties has emerged as a new generation material to replace AHSS and thus to meet the requirements of automobile industries [19]. The base metal microstructure of TRIP steel is mainly constituted with a ferrite matrix along with trace amounts of martensite, bainite, and confined austenite alloys [20]. In plastic bucklings, austenite is converted into martensite to achieve superior extension steels with their excellent combination of strength and ductility [21] and [22].
Henceforth, all the engineering applications which had been used earlier consist of straight lined joint over the levelled surface. The motivation for such variation is that the exceptional characteristics of the laser joint with the close connection between the depth and width of the joint are slightly distorted on the constituent, which can only be achieved
*Corr. Author's Address: Environmental Engineering and Management Research Group, Ton Duc Thang University, Ho Chi Minh City, Vietnam, puttaswamy.madhusudan@tdtu.edu.vn
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through high welding acceleration [23]. Consequently, regarding potential industrial applications of the laser, the variations provide additional applications for laser beam welding in automobile bodies. The high-power concentration of a persistent laser beam offers many advantages over conventional joining techniques for rapid, recurring, high-quality welding of long, straight seams, and axisymmetric mechanism [24] and [25]. Furthermore, the multi-kilowatt neodymium yttrium aluminium garnet (Nd:YAG) lasers are also accessible, with the resilience of fibre optic beam distribution, and their use in the field of complex three-dimensional conversion is increasing [26]. Here, it must be mentioned that the Nd:YAG laser is a substitute beam source, which forms reasonable arrangement solutions for the welding of thin metal sheet production. Nevertheless, it also has defects in geometry, adhering gaps, or inhomogeneities in the material or its exterior that are vulnerable to the charge or generated by previous construction operations [27]. Yang et al. [28] illustrated that in the double-adjoin laser beam welding, the constraint such as incident beam position, beam angle, and beam dissolution distance greatly influence the metallurgical quality of the T-joints.
The laser beam welding (LBW) technique is one of the advanced automated techniques used in recent times. Primarily, there are two main LBW modes: the profound infiltration (or keyhole) welding method and the thermal conduction welding method. Further, the differences in laser wavelength, beam quality, and power induced are accountable for diverse welding development and their outcome [29]. Also, the ultimate tensile strength (UTS) and average yield strength (YS) of the soldered joint were not deprived related to base metal despite their existing softened zone. This claim has been further specified by Rizzi et al [30] who extensively researched laser joining of TRIP, DP, and martensitic steels
Furthermore, Xia et al. [18] engaged laser welding on the Al-alloyed TRIP steel and observed that ferrite was solitary of the prevalent time in the fusion zone due to the ferrite-balance possessions of Al. Nevertheless, related to previous welding procedures, such as arc welding, solid-state welding, induction welding, and friction stir welding, less heat is coupled into the workpiece during laser welding, which arises in a heat-affected zone with low deformation [31] to [34]. To produce multiple phases in steels, with retained austenite (RA), martensite (M), ferrite (F), and tempered martensite (TM), a new heat treatment process was proposed and implemented [35] to [39].
In this manuscript, the laser welding of TRIP steel was explored by the laser beam welding process utilizing a high-quality Nd:YAG laser beam. The characterization of material was investigated, and the influence of different welding conditions, including the angle of the weld, the velocity of laser welding, and power of beam on the strength of the joint, was investigated. Furthermore, the microstructure, tensile behaviour, microhardness of TRIP laser-welded sheets, and their behaviour on the heat-affected zone (HAZ) and fusion zone (FZ) were examined and discussed.
1 MATERIALS AND METHODS
The TRIP steels under investigation were supplied by Nextgen Steels and Alloys Company in the form of a cold-drawn sheet with a thickness of 2 mm. The weld was performed on the transverse direction of the length of the specimen, which is prepared as per the ASTM E8/E8M [40] standards with the desired length. The laser welding setup with a schematic diagram along with the chemical compositions and mechanical properties of as-prepared materials can be obtained from our recent publication [41].
The TRIP steel sheets were welded using a Nd: YAG laser power welding system. The GmbH 56218 series laser machine (Karlich Germany) with three-phase 50 Hz to 60 Hz frequency, maximum power of 13.5 kW, and a 400 V to 480 V ±10 % power source and 900 nm to 1300 nm wavelength laser was used for welding. Furthermore, the butt welding was performed employing an ABB six-axis robot arm, which efficiently handles the welding process with a minimum scrap of 6 kg payload carrying capacity. The welding velocity was kept at 25 mm/s with a power of 2000 W, the beam diameter of 0.6 mm, and a focal distance of 113 m. The welding angle is considered to be 90° for the working table. The experimental setup and laser welding performance are shown in Fig. 1. In a typical experimental section, three different input variables were employed with different permutations and combinations. A sequence numbering system was specified for each sample according to the preparation conditions. The first number specifies the power used in the experiment, while the second number specifies the velocity, and the third number specifies the angle of the laser incident applied in the experiment. As shown in Fig. 2, the first number 1 indicates a laser beam of 1800 W power, while the second number 1 indicates 25 mm/s velocity used and the last number 1 indicates the laser incident angle employed during the experimental setup. Furthermore, the corresponding
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input parameters are tabulated in Table 1. A total of 27 specimens with (33) diagonal array was investigated for different welding parameters, such as the angle of the weld, the velocity of laser welding, and power of beam on strength of the joint.
Fig. 1. Laser welding setup with performing welding of plates
The as-prepared samples were assessed for microstructure at FZ, HAZ, and base metal (BM), along the transverse cross-section of weldments. The cross-sections were mounted in black Bakelite power and heated at 70 °C followed by polishing using different silicon carbide grit paper. After polishing, the samples were further polished with a lapping machine using alumina powder with water. The polished samples were dipped in the 5 % nital solution and 95 % of methanol solution and used for further characterization. The microstructure deformation and
ultimate tensile test were measured using a universal testing machine (UTM), manufactured by SAR Testing Systems with Model No. STS 248 with an operating velocity of 5 mm/min and the precision of the machine is ±1 %. The thermal image was recorded using a Testo 875i thermal imaging camera.
Table 1. Levels of input parameters
Level no.	Power (first digit) [W]	Velocity (second digit) [mm/s]	The angle of laser (third digit) [deg]
1	1800	25	80
2	2000	28	90
3	2200	30	100
1 1 1
/ t \
Power of	Welding	Laser incidend
laser beam	velocity	angle
Fig. 2. A nomenclature system for sample numbering
2 RESULTS AND DISCUSSION 2.1 Microstructure Analysis
The microstructure of TRIP steel is composed of ferrite matrix along with varied fractions of bainite,
Strojniski vestnik - Journal of Mechanical Engineering 67(2021)1-2, 45-52
martensite, and retained austenite. The microstructure of samples 311, 322, and 333 were measured using an optical microscope, Reichert (Austria) and the results are illustrated in Fig. 3. From Fig. 3a, it could be observed that the microstructures predominantly consist of ferrite as base metal throughout the samples and in the welding section, a segregated form of ferrite was observed along with some amount of bainite at weld imperfections with a significant absence of fractures. Furthermore, the measurement of FZ and HAZ zone was calculated on butt joints at three different locations: at the radiation exposure side, a centre of the weld, and the weld root region. As seen in Fig. 3b, the steel structure is divided into three distinct phases: FZ, HAZ, and BM marked as 1, 2, and 3, respectively. The boundary between the BM/HAZ and FZ/HAZ is very well demarcated with colour contrast and grain size boundary difference. Moreover, to understand the surface morphology of the three distinct phases, in Fig. 3b, field emission scanning electron microscopy (FESEM) was conducted, and the results are illustrated in Fig. 3d. From the FESEM images, it can be observed that the grain size distribution in HAZ is quite uniform with rounded smaller voids and less porous, whereas it should be noted that the BM and FZ displayed higher proportion and larger voids than that of the HAZ section.
2.2 Microhardness Analysis
The microhardness was measured using the Everone/ MH-3 testing machine with 1000 gf load and 10 s dwelling time as a standard. The tests were performed at a distance of 0.5 mm from the top surface of the upper plate. When the power was kept at 2200 W, and other parameters are reserved at low conditions, it showed 185 HV1.0/10 hardness, when the other parameters were moved to its higher level, i.e., 30 mm/s velocity and 100° laser incident angle, then the hardness increased to 195 HV1.0/10. Nevertheless, when the power was kept at 1800 W, the hardness value significantly reduced to 110 HV1.0/10 for 90° angle and 116 HV1.0/10 for 100°. It is interesting to observe that when the velocity of the laser beam and laser incident angle were kept constant (i.e., 28 mm/s, and 90° incident angles with 2000 W power), the microhardness value reached 168 HV1.0/10. The corresponding microhardness value concerning the sample condition is shown in Table 2. From the above results, it is obvious that the microhardness value considerably changed as the power of laser welding,
laser incident angle, and laser welding velocity was varied.
Table 2. Microhardness values changing as per the sample condition is different
Sample conditions	Hardness [HV1.0/10]
311	186
333	195
222	168
323	172
112	110
113	116
213	184
322	180
232	180
331	176
2.3 Tensile Strength Analysis
The optimum welding velocity for the prevention of porosity and crumple of the keyhole in weld samples was adopted from the previous publication results [35]. These values are used as a standard to attain the essential weld properties include strengthening at the reverse side of the weld, least allocation in micro-hardness, and homogeneous microstructure. Furthermore, during the joining process, it was observed that the power density for each procedure could be determined from the subsequent equation.
P
HI	Laser
S
nD2 4
(1)
where PLaser is the laser power [W], n is the competence of the laser for low-carbon steel that was measured to be 0.6, while, S is the scan velocity [s], D is the diameter of the laser spot (0.4 mm).
2.3.1 Velocity
During the experimental condition, three different velocities are considered, as discussed previously. As shown in Fig. 4, when velocity is kept constant at 1800 W and indecent angle maintained at 80° and by altering the velocity, the change in maximum load withstand capacity, total strength, and deformations were observed. By altering the velocity load-carrying capacity, an increase in tensile strength with increased elongation was observed. Furthermore, by increasing the velocity from 25 mm/s to 30 mm/s and because of high velocity and rapid cooling of steel weld,
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Fig. 4. The surface plot of maximum load vs.tensile strength and peak elongation for keeping laser power and angle of the weld is constant; a) velocity 25 mm/s, b) velocity 28 mm/s, and c) velocity 30 mm/s (aspect ratio 5:4)
the nature of elongation curve changed from a limp shape to a stiff shape, indicating an increase of tensile strength in as-prepared steel weld.
2.3.2 Laser Power
The power of the welding gun is kept constant at 2.2 kW and the variation was performed in terms of weld velocity and angle of laser incident. The velocities are 25 mm/s, 28 mm/s, and 30 mm/s, and the angle of the laser incident is changed from 80°, 90°, and 100°. As shown in Fig. 5, it could be observed that at 2200 W power and 25 mm/s velocity the tensile strength was decreased with an increase in laser incident angle from
80° to 100°. Furthermore, the deformation changed from 5.5 mm to 5.1 mm with an increase in incident angle. Interestingly, a minor increase in tensile strength was observed when the incident angle was changed from 90° to 100°. Also, as shown in Table 3, the tensile strength increased to 500.98 MPa for a joint prepared at 2.2 kW power, 25 mm/s velocity, and 80° incident angle. As the velocity was changed from 25 mm/s to 28 mm/s, the tensile strength was increased to 531.55 MPa; furthermore, when the incident angle was set to 100o the tensile strength enhanced to 549.19 MPa. When the velocity was increased from 25 mm/s to 28 mm/s and fixing the laser incident angle to 80°, the strength of the steel was improved, in contrast,
Fig. 5. The surface plot of maximum load vs.tensile strength and peak elongation for keeping laser beam velocity and angle of the weld are constant; a) power 1800 W, b) 2000 W and c) 2200 W (aspect ratio 5:4).
Table 3. Variations in tensile strength by changing the velocity of the laser beam
Serial no.	Sample number	Maximum load [N]	Peak elongation [mm]	Break load [N]	Break elongation [mm]	Tensile strength [N/mm2]
1	311	12,524.4	4.8	10,887.8	5.5	500.98
2	312	12,191.2	4.7	11,064.2	5.4	487.65
3	313	12,299.0	4.8	12,034.4	5.1	491.96
4	321	13,897.6	8.5	12,289.2	8.8	531.55
5	322	12,376.6	5.3	11,260.2	5.9	494.71
6	323	10,917.2	4.5	10,035.2	4.5	486.69
7	331	13,729.8	8.9	12,299.0	9.2	549.19
8	332	12,602.8	5.7	10,113.6	6.3	504.11
9	333	12,014.8	4.4	7,379.4	5.2	480.59
An Investigation on Laser Welding Parameters on the Strength of TRIP Steel
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the deformation changed from 5.5 mm to 8.8 mm. When the laser incident angle was set at 100°, the deformation of 9.2 mm was achieved. Interestingly, as the incident angle changed from 80° to 100° the ultimate tensile strength was increased by 9.62 % and in contradiction, the deformation was improved by 67 %. As shown in Table 4, it could be observed that at the laser incident angle of 100°, a lesser deviation occurred in the ultimate tensile strength and deformation. From the experimental results, it could be concluded that as the incident angle is increased the strength and deformation of the welded steel also increased.
Table 4. Angle versus tensile strength difference results
Serial. No.	Angle [°]	Tensile strength difference [MPa]
1	80	30.57 17.65
2	90	7.06 9.41
3	100	-5.27 -8.10
2.4 Finite Element Analysis
The finite element analysis (FEA) is performed using Simufact software and the results show that the failure strength is nearly the same as in the experimental results. For instance, the ultimate strength of sample no 312 is determined to be 487.65 MPa; in contrast to the Simufact software analysis, it is revealed to be 485.18 MPa. These results clearly illustrate that there is an exceptionally less deviation as in software results with the ideal measured conditions [42] and [43]. Furthermore, the finite element modelling (FEM) was performed using Simufact welding software to understand the temperature-dependent thermophysical and mechanical properties of matter. Fig. 6 illustrates the temperature field in the selected time during the laser beam welding of sample number 312 with a laser power of 2200 W, the velocity of the laser beam is 25 mm/s, and the laser incident angle is 90°. The fusion zone is very narrow, and the temperature of the base metal distant from the weld centreline remained practically unchanged. Accordingly, the ultimate tensile strength of welded TRIP steel depending on the input parameters and its thermomechanical treatment showed an ultimate strength of 485.18 MPa. Due to the effect of the laser power, the temperature is very high, but the is transferred to the atmosphere through conduction, convection, radiation; all of this has to be completed within a split of a second. According to
Fig. 6, the nuclear region is associated with a higher yellow zone, which has a higher temperature than other regions. The free end marked in blue indicates the temperature below the merging zone temperature.
Fig. 6. Thermal image capture for sample no. 312 (Scale: 1 mm = 20 mm with actual dimension)
3 CONCLUSIONS
In this manuscript, the TRIP steel joints were characterized to understand their microhardness, tensile strength, and deformation, for laser power, laser incident angle, and laser welding velocity. The experimental result with sample no. 312 showed an ultimate strength of 487.65 MPa, in contrast to the simulation software, which showed the ultimate strength as 485.18 MPa, which is relatively less deviation from the experimental results. Furthermore, from the experimental results, it is clear that the laser incident angle played a substantial role in the enhancement of as-prepared steel strength. The maximum ultimate strength of 549 MPa was observed at an 80° incident angle with 30 mm/s velocity, and 2200 W power. Also, it could be observed that the deformation value and steel strength had increased as the power and velocity increased. Furthermore, our microstructure study illustrated that the microhardness in the fusion zone was increased to 185 HV1.0/10 by increasing the power and keeping the other parameters at a low level.
Nevertheless, by further increasing the power and velocity, the microhardness value could be increased to 195 HV1.0/10. Conversely, if the power is kept at the lower side (i.e., 1800 W), then the microhardness value dropped to 116 HV 1.0/10. The finite element modelling showed no cracks or pores, confirming that as-prepared specimens are less thermally deformed.
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4 ACKNOWLEDGEMENTS
The authors would like to thank Marathwada Mitra Mandal's College of Engineering (MMCOE) Karvenagar for providing characterization equipment. Dr Puttaswamy Madhusudan would like to acknowledge Ton Duc Thang University, Ho Chi Minh City, Vietnam for their financial support.
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Khot Rahul, S. - Venkateshwara Rao, T. - Harshad, N. - Girish, H.N. - Ishigaki, T. - Madhusudan, P.