Effect of CeO2 on microstructures and mechanical properties of welded high-strength steel weld metal

The effect of CeO2 on the microstructures and mechanical properties of welded high-strength steel weld metal was investigated by optical microscopy, scanning electron microscopy and mechanical testing. The results demonstrate that the addition of CeO2 can promote the refinement and spheroidization of inclusions, refine the grains, and form acicular ferrites in the weld metals. When the addition of CeO2 increased from 0% to 3%, the content of bainites gradually decreased, and the lath structure disappeared. The formation of the acicular ferrite ductile phase inhibited the formation of bainites and other strengthened phases in the weld metals, and the microstructure of acicular ferrites was excessive. When the CeO2 content was 1%, the tensile strength was 903 MPa, the yield strength was 848 MPa, and the low-temperature impact toughness was 61 J at −40 °C. When the CeO2 content was 3%, the low-temperature impact toughness of the weld metal gradually increased to a maximum value of 71 J. The weld metal had the highest toughness but the lowest strength. The addition of CeO2 changed the pattern of crack generation, and the fracture mode changed from quasi-cleavage fractures to ductile fractures with dimples. To achieve a good matching of strength and toughness, the wire No. 2 with 1% CeO2 had the best comprehensive mechanical properties.


Introduction
With the progress of science and technology and the development of industrial production, high-strength steels have gradually replaced low-alloy steel and are widely used in various engineering fields, such as aerospace, offshore platforms, and oil pipelines. However, the wide application of high-strength steels is inseparable from the welding technology, so the development of high-strength steel welding consumables and the study of the effects of alloying elements on the microstructure and mechanical properties of weld metals and heat-affected zones are hotspots in the current welding field [1]. Zhang et al [2] studied the effect of acicular ferrite (AF) on the mechanical properties of weld metals. Inclusions can act as inert nucleation surfaces and reduce the activation energy to promote AF nucleation. Mao et al [3] studied the effect of Ni on the microstructure of the weld metals and pointed out that Ni could promote the transformation of the microstructure from granular bainite (GB) to lath bainite and lath martensite, and appropriate Ni could improve the impact toughness. Keehan et al [4] found coalesced bainite in high-strength steel weld metals and noted that coalesced bainite was a coarse and brittle phase, and its presence deteriorated the toughness of the weld metal.
Many scholars [5,6] have studied the microstructure transformation of the weld metals and mainly focused on C, Mn, Cr, Ni, etc. Regarding the role of rare earth elements in metal materials, the research direction focuses on steel modification. At present, there have been few, if any, studies on the effects of rare earth elements on the strength and toughness of welded high-strength steel weld metal. Therefore, rare earth oxide is the research object in this paper, and we conduct a systematic study on the effect of CeO 2 on the microstructures and mechanical properties of welded high-strength steel weld metal. Any further distribution of this work must maintain attribution to the author(s) and the title of the work, journal citation and DOI.

Experimental procedure
To study the effect of CeO 2 on the microstructures and mechanical properties of welded high-strength steel weld metal, three different contents of CeO 2 were added to the metal-powder cored wire: wire No. 2, wire No. 3 and wire No. 4 were added to 1%, 2%, and 3% CeO 2, respectively. The wire 1 (CeO 2 0%) was the control group. The diameter of the wires was 1.2 mm, and the base material was made of Q235 carbon steel. Weld metals were prepared according to the AWS standard A5.29/A5.29 M [7]. An 80Ar+20CO 2 shielding gas was adopted because the composition is widely used in practical engineering applications. The pass arrangement and welding parameters are shown in figure 1(a) and table 1, respectively. The specimens were prepared according to AWS standards A5.29/A5.29 M [7] and B4.0 [8]. The groove weld test assembly for mechanical properties is schematically shown in figure 1(a). The round tensile specimens and Charpy V-notch impact specimens are shown in figures 1(b) and (c). After preparing the standard specimens, the mechanical properties of the weld metals were tested with a WAW-6000 tensile testing machine, and the results of the yield strength, tensile strength, shrinkage and elongation were recorded. The Charpy impact test was performed by an JB30B impact testing machine after the impact specimens were cooled to −40°C. Five impact values were recorded, and the average value was taken after removing the maximal and minimal values. The chemical compositions of the weld metals were determined with a Q4 optical emission spectrometer. Metallographic specimens were prepared and etched with 4% natal. The microstructures of the weld metals were observed using optical microscopy (OM), and the proportion of the microstructure was calculated. The Vickers hardness of the weld metal was measured using a HXD-1000TMSC/LCD Vickers hardness tester. The fracture surfaces were examined by a TESCAN VEGA3 scanning electron microscope (SEM), and the inclusions in the dimples were analyzed by energy dispersive spectrometry (EDS).   Figure 3 illustrates the elongation and shrinkage curves of the weld metals with the addition of various CeO 2 contents. With the addition of CeO 2 , the weld metals had basically identical trends of elongation and shrinkage. Wire No. 3 with 2% CeO 2 had the lowest elongation and shrinkage, which were 9% and 8%, respectively. Wire No. 4 with 3% CeO 2 had the highest elongation and shrinkage, which was 19.6% and 29%, respectively. Figure 4 shows a scatter plot of the Vickers hardness of the weld metals with different CeO2 contents. Wire No. 3 with 2% CeO 2 had the highest Vickers hardness, which was 279 Hv. Wire 4 with 3% CeO 2 had the lowest Vickers hardness, which was 241Hv. Without CeO 2 and with 3% CeO 2 , the Vickers hardness value of the weld metal had a large dispersion, which indicates that the microstructure of the weld metal was not uniform. With the addition of 1% CeO 2 , the dispersion of the weld metal Vickers hardness value was the smallest, which indicates that the weld metal microstructure was uniform.
The microstructure quantitative statistical analysis and microstructure of the weld metals with different CeO 2 contents are shown in table 3 and figure 5. The addition of CeO 2 promoted the nucleation and growth of AF, and the microstructure in the weld metal was gradually refined. Without CeO 2 , the lath microstructure in the weld metals was relatively coarser, as shown in figures 5(a) and (e). With the addition of 1% CeO 2 , the weld metal was composed of martensite (M), B (bainite) and AF, the block microstructure and lath microstructure were reduced, and the microstructure was obviously refined, as shown in figures 5(b) and (f). With further  The addition of CeO 2 can refine the grains and promote the formation of AF in the weld metals. Fine grains have a larger grain boundary area, which helps hinder the dislocation movement. The dislocation movement    cannot easily cross the grain boundaries and accumulate at the grain boundaries, which results in a higher strength of the weld metals [9,10]. In addition, with a more tortuous grain boundary, more energy is required to extend the crack, which is not conducive to the crack extension and can improve the impact toughness of the material. AF is considered an excellent microstructure component to improve the toughness through effective grain refinement, and AF grains can divide large austenite grains into fine individual regions to form a mixed microstructure of fine particles [11]. The AF microstructure has a large-angle grain boundary, which can effectively increase the crack extension path during fracture. The increase in energy required for crack extension helps improve the low-temperature impact toughness of the weld metals, which can explain the higher strength and impact energy of wire 2 than those of wire 1. The grain refinement degree of the weld metal decreases with the addition of excessive CeO 2 , the addition of CeO 2 can be used as the core of AF heterogeneous nucleation, the grain core preferentially attaches to the surface of these impurities and promotes the formation of a large amount of AF, and the formation of a large AF content inhibits the formation of M, B and other phases. M and DUB are the main strengthening phases, which can improve the strength and hardness of the weld metal. AF and GB are toughening phases in the weld metal that mainly improve the low-temperature impact toughness of the weld metal [12]. The excessive formation of AF causes a decrease in M and DUB strengthening phases in the weld metal, so further addition of CeO 2 can cause a decrease in strength and an increase in toughness. This phenomenon was reflected in the micrographs of wire 2, wire 3 and wire 4.

Fracture morphology of weld metals
The fractures of different Charpy V specimens at −40°C are shown in figure 6. With the addition of CeO 2 , the fracture mode changed from quasi-cleavage fracture to ductile fracture with dimples, the tear ridges were scattered between the cleavage fracture and the dimple, the width of the dimples decreased, the depth of the dimples increased, and the distribution of the dimples was even. Dimples could improve the low-temperature impact toughness of the weld metals, which is consistent with the low-temperature impact curve in figure 2. Without CeO 2 , the dimples had the largest width and smallest depth, and the distribution of dimples was extremely uneven and concentrated in a few areas, which shows that the energy absorbed was low and the toughness was poor, as shown in figure 6(a). With the increase in CeO 2 , the dimple width in the fracture of the specimen decreased, the depth increased, and the distribution was more uniform, as shown in figures 6(b) and (c). With the addition of 3% CeO 2 , the number of dimples in the fracture reached the maximum, the dimples were narrow and deepest, and the distribution was the most uniform. There were inclusions in dimples that promoted the nucleation of AF, and wire 1 had the fewest inclusions, as shown in figure 6(a). With the addition of 1% CeO 2 , the number of inclusions increased, and the inclusions were significantly refined, as shown in figure 6(b). With the addition of 3% CeO 2 , there were the most inclusions, and the distribution of inclusions was the most uniform, as shown in figure 6(d). The area of cleavage fracture where the crack source was located in wire 1 was the largest, and the river pattern was smooth and continuous. The cracks started from between the B clusters and propagated along the adjacent B clusters, and the arrow direction was the crack propagation direction, as shown in figure 6(e), which is consistent with the micrograph in figures 5(a) and (e). The left side of two continuous cracks was the crack source generated between the B clusters, the right side was the crack source generated by the decohesion of an inclusion, and the pit after the inclusion fell off appeared at the crack source on the right, as shown in figure 6(f). When the CeO 2 content increased from 1% to 3%, the average area of the cleavage fracture where the crack source was located gradually decreased, the river pattern gradually decreased, the crack source in wire 4 had the smallest average area and smallest river pattern, as shown in figures 6(f)-(h). Figure 7 shows the EDS of inclusions on the fracture surface. The inclusions in dimples were basically spherical. The EDS analysis indicates that the inclusions were mainly composed of Cr, Al, Si, Zr, Ti and trace Ce. The addition of Ce reacted with Al, O, Ti and other elements to form rare earth composite inclusions [13]. The addition of Ce promoted Al 2 O 3 inclusions to be replaced by CeAlO 3 inclusions to form Al 2 O 3 -coated Ce-Al-O rare earth type composite inclusions, which can be used as the nucleation core of TiC and finally form TiC-CeAlO 3 inclusions. Rare earth composite inclusions were formed, and the curved surface of the inclusions was gradually smooth [14]. Figure 6(e) shows the cleavage fracture caused by the boundary cracking of B clusters, which extended to the critical microfracture surface and through the entire specimen. The control condition for crack growth is: σy σf (σy is the normal stress at the front of the gap, and σf is determined by the size of the critical fracture surface). The cleavage fracture mechanism was different from the ductile fracture mechanism; it did not depend on the density of the second phase particles but on the size of the critical microfracture surface controlled by the phase composition of the microstructure. The coarsest B cluster was the weakest area in the microscopic composition, and the critical event of cleavage fracture was confirmed as crack propagation through the boundary of the B cluster. The lath structure was refined with high cleavage fracture stress, which delayed the occurrence of cleavage fracture and improved the impact toughness of the material [15]. In addition, Mao [3]  found that the impact toughness of the weld metal increased, and the river pattern area at the fracture was smaller. He noted that the high-angle grain boundaries in the closely packed B clusters effectively prevented cracks. Figures 6(f)-(h) show the cleavage fracture caused by the decohesion of an inclusion, and the crack initiation was surface shear stress-induced decohesion of the inclusion. The dislocations accumulated at the inclusion particles during material deformation, the cracks initiated and propagated in the inclusion particles at the end of the dislocation accumulation, and the cracks of the inclusion particles that started to crack immediately extended into the matrix grains; then, the cracks extended through the entire specimen. With the addition of CeO 2 , CeO 2 promoted the formation of inclusions and combined with Al, O, Ti and other elements to form rare earth composite inclusions. The thermal diffusivity of rare earth inclusions was more consistent with the matrix, which helped improve the comprehensive mechanical properties of the weld metal. Rare earth inclusions can avoid the generation of additional stress, cause the inclusions to be difficult to separate from the matrix, increase the crack extension energy, and improve the crack extension resistance of the weld metal [16]. In addition, inclusions can promote the formation of AF, and the effective inclusion size for AF nucleation was mainly 1-4 μm [17][18][19]. The observed size of the inclusions in the dimples was 1-2 μm, and the size of the inclusions was within the range of effectively promoting the formation of AF in the weld metal. AF was preferentially nucleated in the grains, which played a role in the segmentation of austenite grains. The growth of DUB was inhibited, the lath of grain was refined, the occurrence of cleavage fracture was delayed, and the toughness was improved. (2) The addition of CeO 2 promoted the formation of rare earth composite inclusions and AF in the weld metal, refined the lath structure, inhibited the formation of M and B, changed the pattern of crack generation and improved the impact toughness of the weld metal.

Conclusions
(3) The optimal proportion of microstructure was found in the weld metal with 1% CeO 2 : AF was 60%, M was 8%, GB was 20%, and DUB was 12%.