Effects of Laser Energy Density On Carbide Dissolution, Element Distribution and Microstructure Evolution of AISI P20 Steel During Laser Surface Quenching

doi:10.21203/rs.3.rs-375133/v1

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Effects of Laser Energy Density On Carbide Dissolution, Element Distribution and Microstructure Evolution of AISI P20 Steel During Laser Surface Quenching

https://doi.org/10.21203/rs.3.rs-375133/v1

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Laser surface quenching (LSQ) was performed on AISI P20 mould and hot-working die steel with an objective to improve surface characteristics. The steel was treated under three different process parameter conditions. The microstructure, element distribution and residual stresses were investigated through SEM, EDS and XRD analyses. The effect of laser energy density on carbide dissolution/ablation, microstructure evolution were thoroughly investigated. The dissolution/ablation of carbides significantly affected the formation of martensite and retained austenite, and the distribution of elements and phase in the microstructure. The results of the study and analyses of treated surface revealed that the LSQ treatment significantly improved the microstructure, eliminated the pores or other defects. Furthermore, the degree of carbide dissolution/ablation was closely related to the laser energy density. Comparing to Cr₇C₃, Cr₃C₂ was more difficult to dissolve at lower laser energy density. Thus, those incompletely dissolved Cr₃C₂ would hinder the growth of austenite and reduce the carbon content in austenite and lead to the formation of low-carbon martensite. The highest laser energy density (150 J/mm²), was able to produce finer microstructure and significantly reduced the inhomogeneity in distribution of Cr between the poor and the rich Cr areas.

Mechanical Engineering

Laser surface treatment

Laser quenching

Carbide dissolution/ablation

Element distribution

AISI P20

Microstructure

As a typical mould and hot-working die steel AISI P20 (3Cr2Mo) is widely used in the plastic mold and the low melting point metal forming die-casting mold due to the excellent combination of properties such as toughness, hardness and comprehensive performances [1-2]. The AISI P20 is commercially supplied in pre-hardened condition to 30-36 HRC, and can be directly employed in molding processing. The service life of molds can reach 500,000 up to times. However, the molds usually fail by surface degradation [3]. When AISI P20 is employed in plastic molds, it encounters a temperature in the range of 200-250 ℃. The molten plastic flows into the mould cavity at a high velocity under high pressure which results in serious friction and abrasion on the surface of cavity [4]. In addition, the strong corrosive gases and vapors (HCl, HF, etc.) produced by the melting and decomposition of plastics can also corrode the mould surface. During moulding and metal forming, AISI P20 steels are also exposed to cycles of repetitive cooling and heating (at temperature of the order of 400-700 ℃) along with severe dynamic/static cyclic load. Such conditions lead a set of severe adverse conditions involving corrosion, erosion, thermal fatigue and abrasive/adhesive wear, etc., and greatly reduce the service life of the molds. [5-6] A surface treatment of AISI P20 to strengthen and hardening up to 57-60 HRC can improve the service life by 1 million times [7]. The adverse service conditions require careful selection of effective treatment process which can effectively control of thickness, hardness, interface bonding and ability to endure the environment. The ideal process not only keeps the original chemical composition of the surface, which saves the production cost caused by the post-treatment, but also brings great economic benefits.

The laser surface quenching (LSQ) and laser melting are among the best of the available alternatives, which can well overcome the shortcomings of conventional surface strengthening processes. In comparison to laser melting, the LSQ can significantly improve the microstructure and surface performances without melting or damaging substrate. Telasang et al. [5, 8] studied the effect of LSQ and laser melting on the microstructure and surface properties of AISI H13, and reported that the LSQ resulted in superior corrosion resistance and mechanical properties with the yield strength improved to as high as 1460 MPa. The authors attributed the overall improvement to the better interface characteristics and the formation of low-carbon martensite in case of LSQ. However, the precipitation of brittle carbide at the grain boundary and presence of dendritic structure in the laser melted samples caused poor corrosion resistance, lack of toughness. The yield strength was also found to be 1310 MPa. Therefore, the better performance in stringent environment has attracted huge interest in the investigations on wear and corrosion resistance of different steels by LSQ, and made a great deal of scientific research achievements [9-11].

The surface properties depend on the microstructure in the quenched zone of the LSQ treated surface, which is characterized by the phase composition, the dissolution and diffusion of the initial carbides, the uniformity of element distribution and state of residual stresses. Niroj Maharjan et al. [12] performed LSQ on AISI 4150 to enhance the corrosion resistance, and reported that formation of uniform protective oxide layer containing Cr in quenched surface was a key factor which resulted in enhancing the corrosion resistance of treated samples by about 3 times. Wei Zhang et al. [13] combined element distribution and microstructure morphology demonstrated that laser heat treatment can effectively dissolve Ti and N elements in the alloy 800H phase. The dissolution significantly reduced the amount of TiN as well as probability of crack initiation. Zhikai Chen et al. [14] reported that the surface performances of 40Cr steel could be improved by LSQ treatment. The authors demonstrated that the resistance to impact abrasive wear of treated samples was improved by 2 times. The results of EDS analysis showed that the SiO₂ and Fe_xO_y particles existed before the scratch, and the larger particles can damage the metal under the impact.

The constituent phases comprising of carbides are the main strengthening phases in the microstructure. The ablation, dissolution and diffusion of carbide during LSQ seriously affects the properties of microstructure in the quenched zone. The C acts as austenite stabilizer, expand the austenitic region significantly, and its effect is about 30 times stronger than Ni [15-16]. The distribution of C leads to uniformity and compactness of microstructure (mainly α-Fe), as well as the uniform transformation of austenite into martensite. The Cr can significantly reduce the intergranular corrosion and improve the resistance to Cl^- corrosion [17-18]. The alloying elements and diverse phase changes encountered during surface treatments produce complex set effects which greatly alter the surface properties. Therefore, a detailed study on the ablation/dissolution of carbides and the diffusion and distribution of elements in the LSQ process is important and useful.

Current work reports a comprehensive analysis on the microstructure characterization of AISI P20 steel surface modified by the LSQ process. Extensive analyses on phase composition, element distribution, residual stress and dissolution/ablation of carbide have been investigated in detail. The effects of the carbide dissolution/ablation on the formation of martensite, retained austenite, and the element distribution were thoroughly investigated. The intrinsic relationships among carbide dissolution/ablation, element distribution, microstructure formation and residual stress were clarified. This work is of great significance for the improvement of LSQ microstructure and the reasonable match between the microstructure and properties.

2.1. Materials

The elemental concentration of AISI P20 steel is given in Table 1. The steel received has been hardened as follows: (a) Heating: the AISI P20 steel was heated to 600 ℃ and kept at this temperature for 2 h; (b) Hardening: heating the steel to 900 ℃ for 1.5 h followed by quenching in oil; (c) Tempering: reheating the steel to 600 ℃, and keeping it at this temperature for 2 h followed by air cooling.

Table 1

Elemental concentration (wt.%) in AISI P20 steel

Elements	C	Cr	Mo	Si	Mn	Ni	S	P	Fe
Composition	0.39	1.95	0.35	0.45	0.6	0.1	0.001	0.012	Bal.

2.2. Laser treatment system and laser surface quenching

The laser treatment system utilized in the experiments is presented in Fig. 1. The IPG YLS-4000 fiber laser produced a Gaussian beam with a wavelength of 1070 nm and a maximum power of 4 kW. The flat-top beam of 25 × 4 mm² was shaped by RayTools AK390 laser quenching head from the Gaussian beam. A digital control system was employed to adjust the processing parameters and to control KUKA KR30HA robotic arm. The workpieces were fastened on the platform and processed by laser.

The surface of three samples were treated by LSQ process under three sets of process parameters given in Table 2. The LSQ modified regions in three samples of AISI P20 was measured as 200 × 25 mm².

Table 2

Process parameters used in laser surface quenching of AISI P20 steel.

Sample	Laser energy density (J/mm²)	Laser power (kW)	Laser scanning speed (mm/s)	The focusing beam (mm²)
#1	150	1.8	3	25 × 4
#2	142	1.7	3
#3	113	1.8	4

2.3. Characterization

Each sample with the size of 20 × 10 × 10 mm³ was cut from the center of each LSQ region (marking in Fig. 1) and were polished by standard metallographic procedure. The microstructure of the polished samples was analyzed using Quanta 400FEG SEM equipped with EDS. The phase identification of the LSQ samples was carried out by using Bruker D8-ADVANCE XRD with Cr radiation, operating at 40 kV and 40 mA. The residual stress measurement was performed by PROTO LXRD SYSTEM XRD with parallel beam and Cr radiation operated at 40 kV and 40 mA.

3.1. Microstructure and phase composition

The LSQ modified surface of steel is found to possess three distinct zones in quenching layers: quenched zone, intermediate zone and thermally affected zone [7, 19]. A detailed analysis of strengthening phases, element and phase distribution in quenched zone shall be important for the process optimization and performance improvement.

The microstructure of the untreated samples and all the three LSQ processed samples is shown in Fig. 2. The microstructure of the untreated steel was found to be comprised of tempered sorbite (Fig. 2 (a)). The microstructure also revealed the presence of small number of pores distributed on the ferrite, which would seriously affect the service life of the AISI P20 steel mold. It is clear from the Fig. 2 (b, c, d) that the pores were eliminated after LSQ treatment and the microstructure of treated samples was significantly improved. This could be attributed to the formation of new austenite grains because of the lattice recombination and elements diffusion during the heating process. The ferrite phase with pores possessed higher phase changing energy, which promoted nucleation and growth of new austenite. This illustrated that the LSQ process was beneficial in eliminating pores. Further, it could be shown that the microstructure of quenched zone was mainly consisted of lath martensite (LM), plate martensite (PM), retained austenite (RA) and a small number of carbide particles. Fig. 2 (b, c) reveals that the more PM with high carbon content distributed in the primary austenite grains in sample #1 than in sample #2, and the blocky RA were disappeared. The primary austenite grains formed during austenitizing in sample #1 were faintly visible and the grains were larger as well. The cooling process promoted rapid nucleation of PM in the primary austenite. Under the influence of cooling rate and alloying elements on Ms line, some untransformed RA still existed between the PM in the primary austenite. For sample #1, the laser power and laser energy density were higher, which resulted in the coarsening of primary austenite grains [18]. Furthermore, the high austenitizing temperature and heating rate caused more alloying elements (such as C) to diffuse into austenite, which helped in the high-carbon PM formation during cooling. The high-carbon PM formation has also been confirmed from the literature [19]. The temperature and heat input were relatively lower in sample #2. In sample #2, carbides were not fully dissolved during the austenitizing and suppressed the growth of austenitic grains, resulting in relatively finer grains. Moreover, the diffusion of alloying elements retarded dissolution of carbon in austenite, which led to the more formation of low-carbon martensite.

A comparison of sample #1, #2 and #3 showed that the sample #3 was comprised of coarse microstructure with poor uniformity, which contained more LM and some blocky RA distributed in a concentrated and local way (as shown in Fig. 2 (d)). The high scanning speed in case of sample #3 also resulted in a lower laser heating temperature [20], which led to lower carbon content in primary austenite and the formation of more LM. The laser power and scanning speed of sample #3 were higher (in comparison to sample #2), but the laser energy density was relatively lower, which reduced the laser-to-matrix interaction time and increased the cooling rate. Such conditions caused the non-uniform of temperature distribution and element diffusion in the localized regions of the quenched zone. Additionally, low carbon in the austenite and high cooling rate are conducive to the formation of low-carbon martensite during the phase change, which was also confirmed by XRD analysis as shown in Fig. 3.

In addition to detail microstructural investigation, XRD analyses were also performed on the surface of quenched zone, as shown in Fig. 3 and Table 3. On comparing the XRD peaks and relevant data between the untreated and LSQ samples, it was evident that the microstructure of the untreated samples contained ferrite, Cr-rich carbides M₇C₃ and M₃C₂. The XRD results of the LSQ samples were consistent with the phase composition observed by SEM, including martensite, retained austenite and a small number of carbides. However, no carbides could be detected in sample #1 and sample #3, which was probably because almost all carbides were dissolved during heating due to the high laser energy density. In comparison to the untreated samples, the XRD peaks of LSQ samples were significantly broadening. The half-height width of the martensite (α-Fe) diffraction peak of sample #1 (0.586) was larger than the ferrite (α-Fe) diffraction peak of untreated sample (0.167), and larger than the martensite (α-Fe) diffraction peak of sample #2 (0.540) and sample #3 (0.531). This indicated that the LSQ process refined microstructure to a larger extent (as shown in Fig. 3). Additionally, broadening of peak was also related to the lattice micro-strain variables generated from the solid-state phase transformation during the heating/cooling process. The peak broadening of the conventional heat treatment is similar to that of laser heat treatment [5]. Therefore, it can be concluded that the broadening of the diffraction peaks of martensite (α-Fe) in this process was mainly caused by the microstructure refinement during the phase changing process. It should be noted that after LSQ, the diffraction peaks of martensite (α-Fe) shifted to the left, in which sample #1 possessed the largest offset (2θ = 44.50°), and the crystal plane spacing d was the largest (as shown in Table 3, d = 2.0343). This may attribute to the fact that the sample #1 was irradiated under high laser energy density (150 J/mm²), more solute atoms (C, Cr, Mo, etc.) dissolved in austenite during austenitization, but these atoms could not precipitate during the rapid cooling, which would enhance the formation of high-carbon martensite. This was also confirmed in the discussion given in section 3.1 (Fig. 2(c)). Furthermore, as shown in Table 3, the diffraction peak area (19993) and peak value of martensite (α-Fe) in sample #1 were the largest, indicating that sample #1 possessed higher crystallinity and contained more high-carbon martensite. The higher the crystallinity, the more regular the arrangement of atoms in the crystal, the greater deformation resistance was obtained [21-22]. For the sample #3, the diffraction peak area (9289) and peak value of martensite (α-Fe) were the smallest, illustrating that the crystallinity of the obtained microstructure was lower, and form less martensite, so that the microstructure uniformity of sample #3 was poor as described in 3.1 (Fig. 2(d)).

Table 3

Analysis data of α-Fe peaks.

	2θ (°)	d (nm)	Height	Area	FWHM (2θ)
Untreated steel	44.73	2.0243	1180	11927	0.167
#1	44.50	2.0343	565	19993	0.586
#2	44.58	2.0310	434	14159	0.540
#3	44.67	2.0268	290	9289	0.531

3.2. Residual stress

The LSQ process is capable of changing the state of internal stresses and strengthening surface. The stress distribution also significantly affects the corrosion and wear resistance. The distribution of residual stress in the longitudinal and transverse directions in the strengthened layer of the LSQ treated surface is shown in Fig. 4. The initial stress on the untreated surface was compressive and the average value of the measured stress was -48.7 MPa. The compressive stress in the as received material would have developed during surface machining. The residual stress was measured on the strengthened layer of the LSQ treated surface and found to compressive in nature and significantly increased (average value: -225.1 MPa). It may be noted that the flat-topped laser employed in this work has a uniform energy distribution across the beam cross section. The surface treated by such a beam generated a residual stress profile which was more or less uniformly distributed in the longitudinal and transverse directions. A large number of carbon atoms diffused into austenite during heating and caused distortion in the face-centered cubic (FCC) structure; on subsequent quenching the martensitic transformation changed the lattice from FCC to body-centered cubic (BCC), which developed high volumetric stress in the already distorted lattice and produced significant compressive stress. An increase in the laser energy density increased the diffusion of C atoms (associated lattice distortion too) and in turn increased the compressive residual stress. Furthermore, in addition to lattice distortion, the increase of laser energy density also promoted the formation of martensite, which also added to the residual stresses. This was also confirmed by the XRD analysis. The compressive residual stress on the surface effectively reduced the fatigue cracks and improved the fatigue and corrosion resistance of the treated surface [23-25].

3.3. Element distribution

The LSQ process usually completes in a very short time, consequently, the alloying elements usually do not get enough time to diffuse evenly, leading to fluctuations in concentration in different areas. This raises concern on the homogeneity of microstructure and surface performances. Fig. 5 shows the results of EDS of the untreated and LSQ treatment AISI P20 steel under different laser energy density. The two key elements of C and Cr were analyzed emphatically here, and the EDS results are listed in Table 4. The distribution of C is indicative of the microstructural homogeneity and distinguish the type of martensite present on sight. Similarly, the distribution of Cr is indicative of microstructural regions of poor or rich chromium which accordingly defines the evaluation of corrosion resistance property (especially to the corrosion of Cl^-).

It is evident from the Fig. 5(a) that the concentration of Cr and C largely varied and were present on the ferrite boundary in the untreated steel. The microstructure of untreated steel was consisted of tempered sorbite and the C and Cr mainly existed as carbides. The laser heating during LSQ caused diffusion/dissolution/redistribution of elements (C and Cr) and the fluctuations in the concentration was evened out (Fig. 5(b, c, d)). A comparison of sample #2 with sample #1, indicated that the distribution of C in sample #1 was more uniform (Fig. 5(b)). Almost all the carbides were dissolved under the effect of higher laser energy density, the higher temperature and the lower scanning speed. These factors also increased the diffusion rate of C, prolonged the effective diffusion time [26] and resulted in uniform distribution of C. The uniform distribution of C enhanced the uniform and dense microstructure, as shown in Fig. 2(b). Combining with the point analysis revealed that the carbon content of RA in sample #1 was the highest in all the samples, which was 1.7% (point A). This indicated that more C atoms diffused into austenite and retained during the austenitizing. Meanwhile, it is also evident that more PM with high carbon content were formed in sample #1. The lower temperature and lower heat input, resulted in some carbides to remain undissolved in sample #2, which caused very high nonuniformity of C distribution than sample #1. Further, the number of C atoms in solid solution was lower which was found to be only 1.1% (point B). The distribution of C in sample #3 was found to be similar to that of untreated steel, with large fluctuation of carbon concentration and poor distribution (refer to Fig. 5(d)). Most of C atoms were found on the body and boundary of RA surrounded by LM. This was attributed to the fact that high scanning speed caused insufficient diffusion of C and significantly affected the uniformity in the microstructure. The distribution of Cr was found to be more uniform after LSQ which was desirable in reducing the local corrosion caused by the presence of a large number of poor chromium regions [12, 17]. Therefore, the corrosion resistance of mold steel can be significantly improved by LSQ treatment.

Table 4

EDS analysis of P1-P3 (wt. %).

	Cr	C	Mn	Si	Fe
Point A	1.5%	1.7%	0.5%	0.2%	96.1%
Point B	1.2%	1.1%	0.5%	0.4%	96.8%
Point C	1.3%	1.3%	0.4%	0.3%	96.7%

3.4. Carbides ablation and microstructure evolution

3.4.1. Carbides ablation

The dissolution/ablation of carbide imparts significant effects on the diffusion and distribution of C. When the laser power is low, there may be some incompletely dissolved carbides remaining in the quenched zone. Fig. 6 shows the high magnification SEM micrographs of two carbides with different shapes which were distributed in the quenched zone in sample #2. The EDS point analysis data (listed in Table 5) and the results of XRD, could confirm that the block shaped carbides (as shown in Fig. 6(a)) were Cr₇C₃. The rod-shaped or elliptic carbides were identified as Cr₃C₂ (as shown in Fig. 6(b)). It can be evident that the irregular ablation layers and the particles which were broken and exfoliated due to ablation exist at the carbide boundary (Fig. 6(a)). The Cr₃C₂has better thermal stability as compared to Cr₇C₃ [27-28]. Consequently, the Cr₃C₂ablated relatively lower and the ablation layer (broken particles characterizing ablation) at the boundary of Cr₃C₂was not obvious (as shown in Fig. 6(b)). Moreover, Cr₇C₃ underwent secondary reaction with C at high temperature and formed Cr₃C₂ (as given by Formula 1) [29-31].

Table 5

EDS analysis of C1-C2 (wt. %).

	Cr	Mn	Si	Fe
C1	86.5%	0.4%	0.5%	3.0%
C2	83.4%	0.3%	0.3%	2.8%

High magnification SEM at the local regions could be effectively utilized in the analysis of undissolved carbides in the quenched zone of each sample (refer to Fig. 7). For sample #2 which was treated with lower laser power, undissolved carbides in the quenched zone were observed, most of which were rod-shaped Cr₃C₂ with high thermal stability (as shown in Fig. 7(b)). In comparison to Cr₇C₃ blocks, the Cr₃C₂ mostly appeared with relatively clear boundaries with slight dissolution/ablation phenomenon (as analyzed and discussed in the Fig. 6 of preceding section). The sample #1 was treated with the highest laser energy density (as shown in Fig. 7(a)), and it did not possess any trace of undissolved carbides in the quenched zone. It can be inferred that almost all the Cr₇C₃ and Cr₃C₂were completely dissolved because of the high heat input and long interaction time. An observation of Fig. 7(c) reveals that more undissolved carbides with irregular shape were present in sample #3, especially the presence of Cr₇C₃with large block shape. The carbides were embedded in the shallow surface of the matrix, and their interface with the matrix appeared fuzzy. In comparison to sample #2, the size of undissolved carbides in sample #3 was larger and the degree of ablation was lower. Furthermore, as the Cr₇C₃generally dissolve completely at about 870 ℃ [32], it can be inferred that the temperature of sample #3 might have reached between Ac1 and Ac3 lines.

3.4.2. Microstructure evolution

Fig. 8 shows the microstructure evolution of the quenched zones treated under different laser energy density. During treatment the irradiation of high energy laser beam heated up the untreated surface rapidly, the nucleation of austenite began at the interface of ferrite and carbides (tempered sorbite) when the temperature exceeded Ac1. During transformation, the C atoms continuously dissolved by diffusion into austenite and promoted the growth of austenite. The diffusion and dissolution is a time and temperature dependent process, and different combinations of LSQ parameters produce conditions of different interaction time and temperatures. Consequently, different heat input and interaction time, results in a very widely different microstructure of the quenched zone. The variations in undissolved carbides, type of transformed martensite, number of RA and the carbon content (as shown in Fig. 8) were produced as a consequence of LSQ treatment under different process parameters.

The sample #2 was treated under the lowest laser power and median laser energy density. The SEM and results of EDS reveal the presence of some undissolved carbides, which restricted the growth of austenite grains and promoted the formation of fine LM with low carbon content. Moreover, if the cooling rate during quenching is lower than the critical cooling rate, some untransformed austenite will be retained. For the sample #1, the laser energy density was the highest, the carbides were fully dissolved, and complete austenitic transformation occurred. This resulted in the formation of high amount of high-carbon PM after cooling. However, the sample #3 was treated at the lowest laser energy density (the scanning speed was highest). Under such a condition, a small number of undissolved carbides were observed in the microstructure. The lower temperature and higher laser scanning speed result in non-uniform element diffusion. The heavily nonuniform diffusion causes the evolution of heterogeneously distributed blocky RA (or ferrite), produces the highly nonuniform microstructure, and the formation of low-carbon LM.

The mechanisms of laser surface quenching involves martensitic strengthening, retained austenite solution strengthening, grain refinement strengthening and residual stress strengthening, etc. The dominant mechanism depends on the phase composition, phase distribution and phase size. The results of studies show that the undissolved carbides in the transformed phase are beneficial in improving the wear resistance property, but the phase interface in multiphase microstructure increases the susceptibility of corrosion and reduces the corrosion resistance [8, 33, 34]. Having demonstrated a widely varied microstructural feature produced under different LSQ conditions, it is importance to select the appropriate processing parameters according to the in-service performance requirements.

LSQ can effectively eliminate the pores and other defects on the original AISI P20 steel surface. PM, LM, RA and some undissolved carbides are the main component of the quenched zone microstructure. Higher laser energy density is beneficial to obtain the uniform and dense microstructure, and to the formation of high-carbon martensite and the elimination of blocky RA and carbides.
The compounds Cr₇C₃and Cr₃C₂are the main carbides in the quenched zone of LSQ samples. Cr₃C₂ is harder to be dissolved and ablated under lower laser energy density irradiation because of its better thermal stability, and those undissolved Cr₃C₂will hinder the austenite growth and enhance the formation of low-carbon martensite. When the laser energy density reaches 150 J/mm², almost all carbides dissolve, and the element distribution is the most uniform in all the samples.
LSQ can implant uniformly distributing residual compression stress and fine the microstructure in the quenched zone. When the laser energy density reaches 150 J/mm², the residual compression stress is the largest, with the average value of about -280.5 Mpa.

Author Contributions Zhuoyuan Li contributed to all parts of this work: Designing the analysis, collecting data, performing analysis, writing paper. Jian Zhang conceived the idea of the paper. All authors contributed to refining the ideas and finalizing this paper.

Acknowledgements This work was supported by the Natural Science Foundation of Zhejiang Province (Grant No. LY20E050026); Postdoctoral Research Foundation of China (Grant No. 2020M672016); Science and Technology Project of Wenzhou City (Grant No. G20190011).

Data Availability Not applicable

Conflict of interest The authors declare that they have no known competition financial interests or personal relationships that could have appeared to influence the work reported in this paper.

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Reviewers invited by journal
03 Apr, 2021
Editor assigned by journal
02 Apr, 2021
First submitted to journal
28 Mar, 2021

You are reading this latest preprint version

Effects of Laser Energy Density On Carbide Dissolution, Element Distribution and Microstructure Evolution of AISI P20 Steel During Laser Surface Quenching

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Version 1

Abstract

Figures

1. Introduction

2. Experimental Procedure

2.1. Materials

2.2. Laser treatment system and laser surface quenching

2.3. Characterization

3. Results And Discussion

3.1. Microstructure and phase composition

3.2. Residual stress

3.3. Element distribution

3.4. Carbides ablation and microstructure evolution

3.4.1. Carbides ablation

3.4.2. Microstructure evolution

4. Conclusion

Declarations

References

Status:

Version 1