Next Article in Journal
Numerical and Experimental Mechanical Analysis of Additively Manufactured Ankle–Foot Orthoses
Previous Article in Journal
Aging Profiles of AlSi7Mg0.6 and AlSi10Mg0.3 Alloys Manufactured via Laser-Powder Bed Fusion: Direct Aging versus T6
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Materials
Volume 15
Issue 17
10.3390/ma15176129
materials-logo
Submit to this Journal Review for this Journal Propose a Special Issue
► Article Menu

Article Menu

share Share announcement Help format_quote Cite question_answer Discuss in SciProfiles thumb_up
...
Endorse textsms
...
Comment
first_page
settings
Order Article Reprints
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Review

Status and Perspective of High-Energy Beam Surface Strengthening: High-Speed Steel

by
Shang Li
1,
Xuanpu Dong
1,*,
Shuren Guo
1,
Xinwang Liu
1,2 and
Huatang Cao
1,*
1
State Key Laboratory of Materials Processing and Die & Mould Technology, School of Materials Science and Engineering, Huazhong University of Science and Technology, Wuhan 430074, China
2
Fujian Science & Technology Innovation Laboratory for Optoelectronic Information of China, Fuzhou 350108, China
*
Authors to whom correspondence should be addressed.
Materials 2022, 15(17), 6129; https://doi.org/10.3390/ma15176129
Submission received: 11 August 2022 / Revised: 27 August 2022 / Accepted: 31 August 2022 / Published: 3 September 2022
(This article belongs to the Special Issue High-Energy Beam Surface Modification of Metallic Materials)
Browse Figures
Versions Notes

Abstract

:
High-speed steel (HSS) is primarily used to manufacture cutting tools and roll materials for various machine tools. Improving the hardness, wear resistance, and corrosion resistance of HSS is of great significance to the development of the manufacturing and tool industries. The high-energy beams, consisting of laser, plasma beam, and electron beam processing (e.g., surface remelting, cladding, and alloying), have the advantageous characteristics of high heat source energy and good surface processing effect. The research status and perspective of the above three processing techniques on the surface properties (in particular, hardness, wear resistance, and corrosion resistance) of HSS is reviewed, and the principles, advantages, and disadvantages of the three strengthening methods are discussed. High-energy beam surface alloying appears to be the most cost-effective of HSS surface strengthening methods and is promising to receive increasing research attentions in the future.

1. Introduction

High-Speed Steel (HSS) is a high-carbon, high-alloy steel containing significant quantities of W, Mo, Cr, Co, V, etc. HSS was developed in 1898 by American engineers F. W. Taylor and J. M. White at Bethlehem Steel Company [1]. Based on their properties, HSS can be divided into low-alloy high-speed steel (HSS-L), ordinary high-speed steel (HSS), and high-performance high-speed steel (HSS-E), as shown in Table 1 [2].
High thermal hardness is the primary performance attribute of HSS. When HSS is cut at high speed, the edge temperature rises to approximately 600 °C and the hardness remains over 55 HRC. Therefore, HSS can keep its high-speed cutting ability and wear resistance at higher temperatures [3], in addition to its adequately high strength, acceptable plasticity and toughness, and high hardenability [4,5,6,7]. Consequently, HSS is widely utilized in the production of various machining tools with large dimensions, fast cutting speeds, heavy loads, and high operating temperatures, such as turning tools, file tools, milling tools, planning tools, broaches, and drills, among others. Additionally, it can be utilized to produce cold and hot dies that require high wear resistance [8,9,10].
The performance requirements for cutting tools and molds have increased in tandem with the performance of processed materials. Therefore, it is necessary to reinforce the material’s surface in order to fulfill the growing processing requirements economically and effectively. It is difficult to match the actual demand by adding element types alone, so it is important to reinforce HSS from a process perspective. The new HSS satisfies the performance demand by altering the elemental compositions. The most common wear-resistant carbide is presumably vanadium carbide, followed by tungsten carbide, molybdenum carbide, alongside chromium carbide and tungsten carbide. The hardest carbides are MC-type carbides. Therefore, vanadium and niobium MC-type carbides are typically used as reinforcing phases in new high-speed steels. Due to the high cost of niobium, high vanadium and high carbon high-speed steels are new advances of modern high-speed steels [11]. For example, CPM10V (CPM-Crucible Particle Metallurgy), W12Cr4V4Mo, W9Cr4V5Co3, and others are shown in Table 1 [12,13,14,15,16,17,18]. In addition to its high wear resistance and toughness, CPM10V steel also possesses excellent toughness and machinability, and is therefore favorably used in the field of cold work tool steel that cannot be solved due to poor wear resistance of other candidates.
The use of high-energy beams (e.g., plasma beams, laser beams, and electron beams) to modify the surfaces of materials is a surface modification technique developed in recent decades [19,20,21]. When the high-energy beam acts on the surface of the workpiece, the energy density is extremely high, the heat-affected zone (HAZ) is small, the heating is rapid, the surface of the workpiece is instantly melted and solidified, and quenching can be achieved, and the surface of the workpiece can be locally strengthened without affecting the structure of the workpiece matrix [22,23,24,25,26]. The heat distortion of the workpiece is minimal, and the process is very controllable. Figure 1 shows a schematic illustration of the three reinforcement approaches (high-energy beam remelting, high-energy beam cladding and high-energy beam surface alloying). As illustrated in Figure 1a, high-energy beam remelting does not alter the elemental composition of the substrate because of no exterior addition of other materials. The high-energy beam rapidly melts and cools the substrate’s surface to facilitate the dissolution, ultimately enhancing the substrate’s characteristics. As shown in Figure 1b, high-energy beam cladding only melts the additional metal powder; the substrate scarcely dissolves. The coating composition is newly added metal, and the improvement in surface performance is dependent on the metallic coating. As seen in Figure 1c, high-energy beam alloying simultaneously melts the substrate and adds metal powder. The composition of the coating changes, and the enhanced performance depends on the properties of the new coating metal created by the new metallurgical reaction. High-energy beam remelting, high-energy beam cladding, and high-energy beam surface alloying processing of interests to summarize the recent advancement of HSS surface strengthening treatment from such three perspectives.

2. Research Progress on the Enhancement of HSS’s Surface Characteristics by High-Energy Beam Remelting

Typically, the principle of using a laser as a heat source for remelting and strengthening HSS is to use laser scanning to heat the surface of the material, which triggers the surface of the substrate to melt and then rely on the self-excited cooling of the substrate material to condense into a hardened layer. Laser sintering of the workpiece surface can refine the microstructure, reduce surface defects, and enhance wear resistance [21]. Similarly, when the high-energy beam is used as a heat source for rapid heating of the workpiece surface, the temperature of the heated part reaches above the phase transition temperature in a very short amount of time and then relies on the workpiece’s own cooling and phase transition to obtain the desired microstructure, thereby achieving excellent surface properties, including high wear resistance and corrosion resistance [27].
As the laser power density can reach 107 W/cm2 and the central temperature of the plasma arc can reach 105–106 K orders of magnitude [28,29], they can be both used as heat sources to scan the heated metal part surface after the substrate melts and cool by self-excited cooling to obtain very fine or ultra-fine grain microstructure and high-hardness carbides. The workpiece’s hardness, wear resistance, corrosion resistance, fatigue resistance, and oxidation resistance are significantly enhanced by the phase hardening layer’s ultrafine grains, exceptionally high dislocation density, and ability to produce compressive stress in the surface layer.

2.1. Research Development of High-Energy Beam Remelting on HSS Surface Hardness

In evaluating the mechanical properties of HSS in service, hardness is one of the most primary performance indicators. Throughout the working process, cutting instruments will be subjected to a variety of strains. Therefore, HSS should have adequate hardness to prevent damage during the high-speed cutting, thereby ensuring processing consistency and work productivity. When a high-energy beam is used to treat the surface of a HSS sample, the surface quenching effect is produced by rapid heating and rapid cooling (102~106 °C/s), which results in the dissolution of carbides and an increase in the carbon content of martensite, significantly increasing the surface hardness of the HSS. The effect of hardness enhancement is summarized in Table 2.
For some HSS such as the substrate, high-energy beam remelting can enhance the surface hardness by about 150 HV. The degree of the increased hardness increases with the high-energy beam’s power. For instance, Chen et al. [42] used W18Cr4V HSS as the substrate, and after laser remelting treatment with 1.2~1.5 kW laser, the transition layer had the highest hardness, 950 HV, which was approximately 150 HV higher than the hardness of the substrate W18Cr4V HSS, and the hardness of the transition layer was further improved after tempering treatment at 640 °C. Tuo et al. [43] used an 800 W laser for laser hardening treatment on the surface of HSS rolls and discovered that the hardness after treatment could reach up to 68.5 HRC, whereas the original hardness of the substrate was 59.2 HRC, yielding an improvement of 15.7%, primarily because the carbides became spherical and evenly distributed in the substrate after laser hardening treatment. Li et al. [44,45] strengthened the surface of M2 HSS with a plasma beam, and the hardness of M2 HSS increased by approximately 150 HV in the near-surface layer of approximately 250 μm under the working condition treatment of an acceleration voltage of 200 kV, beam density of 180 A/cm2, the pulse width of 150 μs, and a number of pulses of 10 times. When the voltage for electron beam acceleration was increased to 40 kV, the beam current density was 200 A/cm2, the pulse width was 5 μs, and there were 9 pulses. The average hardness of M2 HSS has been increased by approximately 118 HV [46]. Chen et al. [47] remelted and strengthened M6 HSS by electron beam, and the average microhardness was 800 HV, which was significantly greater than that of the substrate (283 HV) after spheroidization treatment, consequently the improvement in hardness was evident.
Figure 2 shows the structure of laser-remelted W6 HSS following remelting. As shown in Figure 1a, there are lamellar eutectic carbides in the intergranular interval, and the results of XRD analysis in Figure 2d show that the lamellar eutectic carbides and the fine rod-like carbides at the end of the eutectic phase are M2C (hcp) phase and MC (fcc) phase, respectively. As shown in Figure 2b, a significant amount of acicular martensite was formed within the grains near the remelting zone boundary. As shown in Figure 2c, fine, white, unmelted spherical carbides are present in the middle of the reticulated carbides near the remelting zone boundary. Because of the rapid cooling rate at the boundary during remelting, dissolved carbide cannot disperse, and the melting and solidification process is completed in the original location. In the process of high energy beam remelting, when the high energy beam irradiates the surface of the HSS, the remelting zone undergoes considerable structural changes. The original bulk carbide decomposes and becomes uniformly distributed, the mesh carbide is produced at the grain border, and the needle martensite is produced within the grain (see Figure 2b). In addition, the alloying elements form a complex segregation zone which promotes the development of brittle carbides and reticulated carbides at the grain boundaries, and the hardness of the metal in the remelting zone increases substantially. Adjusting the power and scanning speed of the high-energy beam to control the precipitation of carbide and martensite production in the remelting zone becomes the primary method for increasing the surface hardness of HSS through the high-energy beam remelting process.

2.2. High-Energy Beam Remelting Surface to Improve the Wear Resistance of HSS

Wear resistance is the capacity to withstand wear. Due to the high precision and efficiency requirements of HSS tool processing, it is vital to preserving the extremely precise size and surface roughness of the tool. Therefore, wear resistance is crucial for ensuring the cutting quality of its mechanical qualities. High temperature and heat resistance, comprising high temperature hardness and microstructure stability, are the primary determinants of wear resistance. Similarly, the morphology, size, and distribution of carbide in the microstructure have a substantial effect on the wear resistance of HSS. To some extent, the wear resistance of HSS increases proportionally with its hardness. However, once the hardness reaches a certain value, the wear resistance no longer varies with the uplift of hardness, and instead it decreases when the increase in hardness of HSS causes its brittleness [48].
The treatment of high energy beam remelting increases the wear resistance of different HSS surfaces by a factor ranging from 2 to 10. Chen et al. [42] employed W18Cr4V HSS as the substrate, and after laser remelting treatment with a power of 1500 W, a scanning speed of 5.4 mm/s, and tempering treatment at 640 °C, the wear resistance of HSS was greatly enhanced. As shown in Figure 3, the wear volume of W18Cr4V HSS treated by laser remelting + tempering at 640 °C was approximately one-tenth that of conventionally quenched and tempered W18Cr4V HSS. Li et al. [45] fortified the surface of M2 HSS with ion beam, and the test wear volume of M2 HSS was reduced from 16 mg to 9 mg under the working condition treatment of accelerating voltage of 200 kV, beam density of 180 A/cm2, pulse width of 150 μs, and pulse number 10 times, indicating that the wear resistance of M2 HSS was enhanced by nearly 2 times after ion beam remelting treatment. When Mei et al. [49] modified the working circumstances to an accelerating voltage of 250 kV, a beam current density of 160 A/cm2, a pulse width of 80–100 ns, and a pulse count of 5, the authors reached similar conclusions for the treated M2 HSS, but the treated layer was reduced from 250 μm to 200 μm. SEM images of the surface morphologies of HSS before and after the high intensity pulsed ion beam (HIPIB) irradiation treatment are shown in Figure 4. After HIPIB treatment, certain crater-like craters occur on the surface of HSS, as shown in the image. The number of craters continues to diminish as the number of treatments increases, and the craters’ borders become less distinct (see Figure 4b–d). Liao et al. [50] treated the surface of M42 HSS with pulsed explosion plasma and discovered that a pulse count of 2 provided the greatest increase in wear resistance. After treatment, the test wear loss decreased from 2.6 mg to 0.5 mg, indicating that the wear resistance of M42 increased almost 5 times. Yu et al. [51] tested M2 HSS with a pulsed blast-plasma beam and discovered that at 10 pulses, the surface wear performance of M2 HSS was enhanced by 2.3 times.
Quick heating, melting, and rapid cooling generate a new structural layer on the surface of the material during high energy beam remelting, resulting in grain refinement. The refinement of grains prevents the creation and growth of wear cracks, while the transition of α-Fe to γ-Fe in the treated surface and the generation of a high number of defects [49] such as dislocations enhance the surface wear resistance of the material.

2.3. High-Energy Beam Remelting Enhances Corrosion Resistance of HSS Surfaces

The corrosion resistance refers to the capacity to resist corrosion, as HSS is frequently used as a manufacturing tool for use in hostile environments. Therefore, corrosion resistance assures the durability of HSS in extreme service conditions and prevents the inaccurate size, high surface roughness, and other mechanical qualities of HSS-made tools caused by corrosion elements in the environment.
Li et al. [46] surface modified M2 HSS with an electron beam acceleration voltage of 40 kV, beam current density of 200 A/cm2, pulse width of 5 s, and number of pulses of 9 under working conditions, and then conducted corrosion tests. They discovered that the corrosion increment decreased from 0.0016 g to 0.0011 g, and the corrosion resistance of remelted HSS was significantly enhanced. Yu et al. [51] showed that after 10 pulses of treatment with a pulsed explosion-plasma beam, the corrosion resistance of M2 HSS was greatly enhanced. The dynamic potential polarization curves of M2 HSS before and after plasma detonation treatment (PDT) are shown in Figure 5. After 10 pulses of PDT treatment, the self-corrosion potential of the PDT sample increased from −0.590 V to −0.510 V; the corrosion rate of the PDT sample was 8.27 × 10−4 mm/a, and the self-corrosion current density was 3.508 × 10−5 mA/cm2; the corrosion rate of M2 HSS is 3.81 × 10−3 mm/a, and the self-corrosion current density is 1.865 × 10−4 mA/cm2. It can be seen that the corrosion resistance of M2 HSS is obviously improved after PDT treatment. The surface layer of untreated M2 HSS is predominantly formed of martensite α′-Fe and MC (M is mainly W and Cr). The surface of M2 HSS underwent a change from martensite α′-Fe to austenite γ-Fe with a fcc structure after PDT treatment, which is because the surface carbides of the HSS are dissolved and disseminated during the quick heating process, and during the rapid cooling process, the high-temperature liquid-phase austenite remains at normal temperature and the carbides are solid-dissolved within the interior austenite.
Pitting corrosion is a common kind of corrosion on metal surfaces. The pitting corrosion is strongly attributed to the material inhomogeneity (casting defects, differences in grain structure, inclusions, gran boundary defects, etc.) on the surface of the metal sample. The predominant cracking initiation caused by pitting corrosion can be correlated to the primary austenite grain boundaries, as these sites are normally weaker in martensitic steels. Furthermore, the formation of carbide chains can also result in faster crack propagation along the incoherent boundaries. Figure 6 shows the final size and shape of the M35 HSS pitting, which expanded from a small, localized pit to a single, huge pit. The majority of the expansion of the pits is vertical, and the main pit shape is elliptical with higher depth. As shown in Equation (1), Matic J K et al. performed a Weibull distribution of the relative size of pits on the distribution and influence of corrosion propagation over time, where β is the shape parameter (Weibull slope) and η is the scale parameter. It was found that metals with a smaller structure and more network structure have a higher corrosion resistance, and the emergence of corrosion pits is slower [30]. Due to the high energy of the heat source of the high-energy beam, the impurities adsorbed on the surface of the HSS evaporated or vaporized, hence reducing the hazards of pitting corrosion and increasing the material’s corrosion resistance. The corrosion resistance of HSS is proportional to the austenitic γ-Fe content of its surface layer [31,32]. During tip discharge, the W electrode rod is partially vaporized, and W elements infiltrate the surface of HSS, which increases the material’s corrosion resistance [33,34].
f ( t ) ≡ β η ( t η ) β − 1 e − ( t η ) β
Kwok C T et al. [35] carried out laser remelting on the surfaces of M2, ASP23, and ASP30 HSS, and discovered that the corrosion current density was decreased and the corrosion resistance of HSS was strengthened. The combined effect of refinement of bulky carbides in the HSS microstructure and higher solubility of passivating alloys in austenite and martensite, as a result of laser remelting, enhanced the corrosion resistance of HSS, with ASP-23 HSS exhibiting the highest corrosion resistance after laser remelting. Optical images of cross-sectional appearance and the SEM images of the melting zone (MZ)of the laser-melted specimens (LMS) are shown in Figure 7.
As shown in Figure 7a,c,e, in the regions where successive laser tracks overlapped, the melted surfaces of all specimens were relatively smooth and devoid of fissures. Figure 7b shows the SEM image of the LSM-M2 melting zone. At the interdendritic boundaries, a continuous network of eutectic carbides (γ–K) was observed, and the dendrites consisted of γ and α′. In contrast, LSM-ASP23 and LSM-ASP30 exhibited a more homogeneous and finer dendritic or cellular structure of γ and α′ (Figure 7d,f).

3. Research Advancements Concerning the Improvement of the Surface Properties of HSS by High-Energy Beam Cladding

High-energy beam surface cladding technology is an emerging metal surface modification and surface treatment technology that utilizes high-energy beams as a heat source to fuse a coating with wear, heat, and corrosion resistance properties to the surface of a substrate material via rapid melting, expansion, and instantaneous solidification, with cooling rates typically reaching 102~106 °C/s, thus constituting a new composite gradient material. The coating has a high bonding strength, a dense coating structure, low porosity, and few impurities [52]. When the surface is melted by the high-energy beam, only the full precoat is melted, while the surface of the substrate is only partially remelted, preserving the precoat’s composition [53]. Only a thick band of approximately 5 μm at the substrate bond is diluted. Due to HSS’s high hot hardness, wear resistance, and other benefits, researchers use powder or wire containing HSS components to strengthen the base material by cladding, thus altering the surface properties of the base material.
High-energy beam surface cladding is a rapid and stable method for producing HSS coatings of diverse material compositions on the surface of an inferior substrate (e.g., carbon steels or cast irons) by adding featured powder materials, which can drastically alter the substrate’s properties while decreasing the cost of employing precious bulk metals. Currently, surface coating cladding technology for high-energy beams is a popular direction, but there is always room for improvement. Future research will focus on the automation of energy control of high energy beams, the influence of various protective gases on high energy beam surface cladding, the composition of coating materials, and the integrity of process equipment. Some metal elements in HSS have high melting temperatures, therefore utilizing a high-energy beam as a heat source for cladding enables the HSS powder or wire to cover the surface of the substrate more uniformly and efficiently.

3.1. High-Energy Beam Cladding Research on Surface Hardness of HSS

M2 HSS is a molybdenum-based HSS with minimal carbide inhomogeneity and high toughness. Its powder is frequently used as a raw material to melt and coat other metal surfaces due to its high hardness and wear resistance. There are a huge number of MC, M2C, M6C, and other compound carbides in the newly produced coating, which significantly boosts its hardness. L. Bourithis et al. [54] synthesized an M2 HSS alloy layer with a homogeneous distribution of alloying elements, a thickness of 1.2–1.5 mm, and a microhardness of 759 HV0.2 on carbon steel using a transfer plasma arc (PTA). The alloy layer consisted of martensitic and austenitic dendritic crystals, as well as M6C and M2C composite carbides, as shown in Figure 8. Zhang et al. [55] clad 966T high hardness wire on M2 HSS base material to provide clad layer microstructure without grain coarsening and with a hardness greater than 60 HRC. Tang et al. [56] fabricated an M2 HSS coating using laser cladding technology; the coating’s solidification microstructure consisted of a martensite matrix, residual austenite, and M2C-type carbide; the residual austenite in the coating was essentially eliminated after tempering; and the tempering peak hardness was 813 HV0.5. The TEM characterization and the corresponding SAED pattern of the HSS coatings after triple-tempering at 530 °C are shown in Figure 9. As shown in Figure 9a–c, the coating is slate-like martensite after tempering, and the matrix is uniformly dispersed with nanoscale carbides resembling short rods. Figure 9d shows the SAED pattern corresponding to Figure 9b, which displays two sets of diffraction spots at the martensite matrix position, i.e., the slate-martensite and M2C phases of the hexagonal crystal structure. The orientation of the nanoscale precipitated carbide precipitated on the martensite matrix is identical to that of the martensite matrix. After triple tempering, the lattice constants a and c of the hexagonal M2C phase in the coating fell to 0.2923 nm and 0.4745 nm, respectively, from 0.3011 nm and 0.4771 nm. Zheng et al. [57] determined that laser power of 1900 W, melting speed of 35 m/min, and melting channel spacing of 0.35 mm were the best combinations of parameters for the preparation of M2 coatings by ultra-high-speed laser melting technology, and the prepared M2 clad layer contained a large amount of residual austenite and less carbide content, mainly sub-stable M2C and a small amount of MC carbide, so that the coating hardness was high and the coating’s hardness and wear resistance are much superior to those of the matrix. The specimen cross-sectional shapes are shown in Figure 10. Compared to the various cladding speeds, the width of the cladding tracks, and the laser power, it was discovered that as the cladding speed increased, the aspect ratio increased more dramatically and the surface curvature of the single-lane melting layer became smoother. The effect of laser power and the spacing of the cladding tracks on the width and height of the cladding is minimal. The depth of the cladding is significantly affected. The cladding depth increases with the width of the cladding channel and the laser intensity.
In addition to M2 HSS, various HSS powders, such as Fe-Co-Mo HSS powder and high vanadium HSS powder, can be utilized to increase the surface hardness of a substrate. Xiong et al. [36] developed Fe-Co-Mo HSS coatings on 40Cr substrates with water-atomized alloy powder as the raw material using the simultaneous powder-feeding laser cladding approach. After post-treatment, the coatings’ hardness could reach 900~950 HV0.2. Rahmana et al. [37] laser-melted HSS material onto the surface of 42CrMo4 and discovered that the addition of Co elements to Fe-Cr-Mo-W-V sacrificed Fe (Febal-x-Cr-Mo-W-V-Cox), which significantly boosted the coating’s overall hardness. Different carbides present in the laser cladded HSS alloys are shown in Figure 11. EDS maps and a BSE image revealed that MC carbides are rich in V and have blocky, circular, and rod-like shapes (VC). M2C carbides have a feathery, lamellar, and layered morphology and are enriched with Mo (Mo2C), Mo-containing carbides (Mo2C) have a crystalline structure. Fine Cr-enriched secondary precipitates of M7C3 and M23C6 are interspersed throughout the matrix.
The technology for melting HSS powder with a high-energy beam consists of melting the existing HSS powder on the surface of the base material. The processed metal covering inherits the hardness characteristics of HSS, while the base material retains its own strength and toughness, so the new metal possesses a variety of good attributes simultaneously and may satisfy more complex needs.

3.2. High-Energy Beam Cladding Research on Surface Wear Resistance of HSS

In the high-energy beam melting of HSS coatings, due to the high energy of the high-energy beam, the time required for melting and solidification of HSS powder is very short; as a result, the microstructure grains in the melted HSS coating are fine and not fully grown, thereby achieving the effect of grain refinement. Fine grains and strong carbide particles confer high wear resistance to the HSS coating.
On the surface of the base material, high-energy beam cladding of HSS is utilized, and the hard carbide particles and grain refinement in the coating significantly improve its wear resistance. N. Ur Rahmana et al. [38] discovered that the fine microstructure of laser-coated HSS alloys at 25 °C decreased the contribution of abrasives to wear in comparison to cast HSS. Sun et al. [39] clad austenitic stainless steel’s surface with a molten M3:2 HSS coating, and heat treatment increased the coating’s wear resistance. During dry sliding friction at 500 °C, the maximum wear resistance of the M3:2 HSS coating was attained. Cao et al. [40] fused a high vanadium HVHSS coating onto a ductile cast iron using a high-energy plasma beam; the HVHSS coating exhibited excellent frictional properties due to the mixed hard phases formed by MC, M7C3, M23C6, martensite, and grain refinement; and the hard carbide particles acted as a barrier against abrasion and adhesive wear. The wear morphologies of different samples are shown in Figure 12. It clearly shows the wear morphologies of the HVHSS surface are rather shallow and smooth without brittle failures compared to those of remelted duction iron, Mn13 steel, and the iron substrate, respectively. By laser melting and remelting the Fe82Cr16SiB coating, Liu et al. [58] were able to reduce the friction coefficient and improve the wear resistance due to the increased flatness and crystal grain refinement within the coating after the remelting treatment. As shown in Figure 13a,b, the average size of dendrites decreases down from 3~5 μm of the extreme high-speed laser cladded specimen (EHLA) to 1~2 μm of the laser cladded specimen (EHLA-LR). The friction test results of the coating are shown in Figure 13c–f. As shown in Figure 13c, the wear scar width of the extreme high-speed laser remelted specimen (EHLA-LR) is increased, with respect to that of the extreme high-speed laser cladded specimen (EHLA), while the wear rate decreases slightly. Figure 13d–f show the appearance of wear. On the EHLA and EHLA-LR, the substrate has a furrow morphology, indicative of abrasive wear, together with a high amount of spalling.
To further enhance the effect of grain refinement by controlling the energy and action time of the high-energy beam and to increase the proportional content of wear-resistant metals in HSS powder will be the focus of future efforts to improve the wear resistance of HSS surface by high-energy beam melting.

3.3. High-Energy Beam Cladding Research on Surface Corrosion Resistance of HSS

In the high energy beam melting of HSS coating, the time required for melting and solidification of HSS powder is very short due to the high energy beam. Therefore, with cladded HSS coating, the microstructure grains are fine and not fully developed, resulting in a grain refining effect. Fine grains and strong carbide particles confer high wear resistance to the HSS coating.
Fang et al. [41] utilized a laser fusion coated Fe-0.5Cr-11Cr alloy coating because to the coating’s finer carbide dispersion and consistent structure. The high Cr content of the coating increased the self and pitting corrosion potentials and decreased the size passivation current density, hence enhancing the material’s corrosion resistance.

4. Research Work on the Enhancement of HSS’s Surface Characteristics by High-Energy Beam Surface Alloying

High-energy beam surface alloying is the use of a high-energy beam to melt the metal surface while adding an alloy coating to form a layer of fairly high concentration and fairly uniform alloy layer based on alloying elements as solute and substrate as the solvent, thereby obtaining the required special properties such as wear resistance, corrosion resistance, high temperature resistance, and oxidation resistance, as well as performance beyond the limit of material performance.
The primary distinction between surface alloying and surface cladding is that alloying causes the added alloying elements and a portion of the base material to melt and then undergo a chemical metallurgical reaction in the molten pool; the pre-set coating components are completely diluted (dilution rate = 1). The amount of coating required for surface alloying is only 1/7–1/3 of that required for surface cladding, after industrial requirements are met. It is more efficient and economical. In recent years, it has become an increasingly important research center.

4.1. Research Advancements Concerning the Surface Hardness of HSS by Means of High-Energy Beam Surface Alloying

The metal elements W, V, and Co have high thermal hardness; the hardness of the metal can be significantly increased by pre-placing powder containing these three elements on the surface of HSS and then alloying the surface with a high-energy beam. Under the action of the high-energy beam, the alloying elements in the powder on the surface of the material and the matrix material undergo a metallurgical reaction to form a large number of hardened phases, increasing the hardness of the material. Chen et al. [59,60] melted WC/Co powder on a M2 HSS tool using 1100 W of laser power and 3 mm/s of scanning speed. The average microhardness of the tool’s molten layer reached 1311 HV with many new hard phases, and the average hardness reached 60.24 HRC at 600 °C and still above 50 HRC at 1000 °C. The SEM images of cross section of the alloying layer of sample are shown in Figure 14. From Figure 14a, it can be seen that the cross-sectional structure can be divided into four parts: the cladding region, the bonding region, the heat-affected region, and the substrate. Figure 14b shows that the microstructure is more complex and eutectic, which is mostly the result of the melting pool’s cooling circumstances. Wu et al. [61] fabricated a laser-clad chipbreaker with M2 HSS as the base material and M2/WC-12Co powder, achieving good metallurgical bonding of the materials, no crack flaws in the clad layer, and hardness of up to 907.2 HV. Cao et al. [62,63,64] fused a high-vanadium HVHSS coating onto ductile cast iron using a high-energy plasma beam. The maximum hardness of the coating was 956.5 HV0.2, 4.8 times that of the substrate, due to precipitation strengthening of the hard carbide phase, solid solution hardening of the alloying elements, and fine grain hardening due to rapid solidification caused by rapid heating of the plasma beam. Due to the complexation of ultrafine MC and hard phases such as M2C, M7C3, M23C6, and martensite, the alloying procedure results in a substantial increase in material hardness within a thickness of 800 μm, as shown in Figure 15. It can be seen from Figure 15 that the average microhardness of AZ varies from ~620 HV0.1 to 960 HV0.1, marginally lower than that of the melting zone MZ. The SEM image, EDS area mapping, TEM images, and SADPs in the coating are shown in Figure 16 and Figure 17, respectively. As can be seen from Figure 16, dense, globular MC carbides are dispersed in the top AZ and substantial amount of needle-like martensite as a hard buffer layer to further support the top AZ to increase the wear life. From Figure 17, the MC type-carbide sever as the nucleation sites for other carbides and the TiC carbide held a crystal orientation relationship with V8C7. It can be concluded that the graded coating created by the alloying process has very fine MC carbides due to the in-situ formation of exterior strong carbide-forming elements with the C elements from the iron substrate, and the production of a large number of strengthening phases in the coating significantly increases the surface hardness of ductile iron (Figure 15). Figure 16d,e also indicate a strong physical metallurgical bonding between the HVHSS coating with the substrate.
During the alloying process on the high-energy beam’s surface, W generates primarily M6C-type carbides in the coating and is the primary component of eutectic carbides. V is predominantly present in the coating as VC, with a tiny amount dissolved in other forms of carbides; V can refine the grain and inhibit the decomposition of martensite, hence enhancing the coating’s hardness. Co’s strong connection with W and Mo atoms retards carbide precipitation and aggregation growth and boosts the alloy’s thermal toughness. However, W, V, and Co can have negative impacts on HSS coatings. Therefore, future research will concentrate on their additive ratios.

4.2. Research Advancements Concerning the Surface Wear Resistance of HSS by Means of High-Energy Beam Surface Alloying

The presence of Mo and V in metal elements significantly improves alloys’ resistance to wear. Both components are capable of refining the grain and enhancing the precipitation of hard phases in the alloy, hence enhancing its wear resistance. Consequently, the wear resistance of the metal can be significantly enhanced by alloying the surface of HSS with a high-energy beam and a powder containing Mo and V elements.
Wang et al. [65] prepared Ni-based WC alloying on the surface of M2 HSS and discovered that the precipitated graphite and the Ni metal contained within itself have good friction reduction effects, and that the mechanism for friction reduction is the mutual combination of the soft matrix and the hard phase. As illustrated in Figure 18, Ripoll M R et al. [66] laser deposited various amounts of Nb on the surface of HSS and discovered that following elemental alloying, the wear resistance increase of the HSS surface was greatest when the content of Nb was 1 wt.%.

4.3. Research Advancements Concerning the Surface Corrosion Resistance of HSS by Means of High-Energy Beam Surface Alloying

The addition of Cr in metal constituents can significantly improve the alloy’s corrosion resistance. In the alloy microstructure, Cr is nearly totally dissolved in austenite, which improves the alloy’s hardenability and boosts its corrosion resistance and oxidation resistance. By adding Cr to the powder of the preset powder, the corrosion resistance of the alloy layer formed after alloying on the surface of the high-energy beam can be enhanced. Due to the high energy of the high-energy beam, which melts and vaporizes the impurities, the resulting alloy layer has a thick structure, which lowers the chance of pitting corrosion.
Ripoll et al. [66] deposited various amounts of Nb on the surface of HSS and discovered that following elemental alloying, the best corrosion resistance improvement of the HSS surface was attained when the amount of Nb was 3 wt.%. Nb has a greater affinity for carbon than chromium, and as the Nb percentage rises, less carbon is generated from chromium carbide, therefore less chromium is dissolved in the matrix as an element, thereby enhancing the corrosion resistance of the alloy layer. Figure 19 shows a SEM image of the alloy layer following a corrosion test. The corrosion layer developed on the hard surface of reference was discontinuous and possessed a “mud crack” character (Figure 19a) and has a low density and considerable porosity (see Figure 19b). As the Nb content rises, the scale layer becomes denser, more continuous, and less uncovered by corrosion products (Figure 19c,d). Liu et al. [67] carried out alloying treatment on the surface of carbon steel, and the added materials were HSS and other three kinds of welding wires. Figure 20a,b shows the Nyquist curves of different materials. The impedance spectroscopy exhibits a large semicircular capacitive loop, signifying that the surface film is made of a single layer. The capacitive behavior of surface-modified materials falls in the medium frequency range from 100 to 101 Hz, whereas the medium frequency range of HSS alloys is from 101 to 102 Hz. The HSS alloy peak value is lower than that of carbon steel claddings, indicating the decay of the surface film’s capacitive impedance. Figure 20c shows the equivalent circuit. In this equivalent circuit, Rs is the solution resistance; Rf represents the passive film’s resistance; the constant phase element (CPE) refers to the film capacitance.

5. Summary and Outlook

Since its invention, HSS has expanded swiftly into a wide variety of forms, and is currently undergoing a period of sustained growth. Changing the ratio of metal elements in HSS has limited effect, and it is difficult to match the growing demand. Because of its low material demand and stronger surface requirements, high-energy beam surface strengthening technology has become increasingly attractive for further strengthening HSS surface properties. Due to the fact that it only remelts the surface of HSS substrates, high-energy beam remelting technology offers a moderate performance increase economically and effectively. Furthermore, by utilizing the superior performance of HSS characteristics, high-energy beam cladding technology can be utilized to clad HSS powder onto different metallic substrates, thereby enhancing the overall surface performance of inferior substrates. However, the link between the HSS coating and the substrate is somewhat weak due to the fact that only the packed powder is melted by the melting method. Because the filled powder is melted metallurgically with the base material, high-energy beam surface alloying process consumes less powder and is thus less costly. Additionally, the reinforced layer is more stable and adhesive with the substrate as a result of in-situ formation of metallurgical bonding. Compared to surface remelting, cladding, and alloying, remelting is performed just on the surface of matrix HSS. No new elements are added, and performance is enhanced by altering the structure. During the cladding process, the coating is a newly added material, the matrix barely melts, and the degree of reinforcement depends on the newly added material. The surface alloying is in between; a portion of the matrix and the extra powder are simultaneously melted, and the metallurgical process is carried out. The degree of strengthening is dependent on the quality of the matrix and the addition of powder to regenerate the material by metallurgy. Therefore, high-energy beam surface alloying process will be a potential strengthening technology for HSS-related materials in the near future.

Author Contributions

Conceptualization and methodology, S.L., X.D., S.G., X.L. and H.C.; Software, S.L. and S.G.; Investigation, S.L. and H.C.; Resources, X.D. and H.C.; Data curation, S.L. and S.G.; Writing—Original draft preparation, S.L., S.G. and H.C.; Writing—Review and editing, S.L., X.L., H.C. and X.D.; Supervision, X.D. and H.C.; Project administration, H.C. All authors have read and agreed to the published version of the manuscript.

Funding

Independent Deployment of Scientific Research Projects of Mindu Innovation Laboratory (grant number 2021ZZ123).

Informed Consent Statement

Not applicable.

Data Availability Statement

Not applicable.

Conflicts of Interest

The authors declare no conflict of interest.

References

  1. Townsend, A.S. Alloy tool steels and the development of high-speed steel. Trans. Am. Soc. Steel Treat. 1933, 21, 769–795. [Google Scholar]
  2. GB/T 9943-2008; High Speed Steel. China National Standardization Management Committee. Standards Press of China: Beijing, China, 2008.
  3. Wang, J. Study of the Organization and Properties of M35 High-Speed Steel Containing Nitrogen; Kunming University of Science and Technology: Kunming, China, 2016. [Google Scholar]
  4. Ren, X.; Fu, H.; Xing, J.; Yi, Y. Effect of solidification rate on microstructure and toughness of Ca-Ti modified high boron high speed steel. Mater. Sci. Eng. A 2018, 742, 617–627. [Google Scholar] [CrossRef]
  5. García, C.; Romero, A.; Herranz, G.; Blanco, Y.; Martin, F. Effect of vanadium carbide on dry sliding wear behavior of powder metallurgy AISI M2 high speed steel processed by concentrated solar energy. Mater. Charact. 2016, 121, 175–186. [Google Scholar] [CrossRef]
  6. Zhou, X.-F.; Liu, D.; Zhu, W.-L.; Fang, F.; Tu, Y.-Y.; Jiang, J.-Q. Morphology, microstructure and decomposition behavior of M2C carbides in high speed steel. J. Iron Steel Res. Int. 2017, 24, 43–49. [Google Scholar] [CrossRef]
  7. Ma, K.; Yang, F.L.; Huang, K.; Guo, L. Effects of quenching methods on microstructure and properties of M42 high speed steel. Mater. Sci. Eng. Powder Metall. 2014, 19, 241. [Google Scholar]
  8. Tang, H.; Zhang, H.; Chen, L.; Guo, S. Novel laser rapidly solidified medium-entropy high speed steel coatings with enhanced hot wear resistance. J. Alloys Compd. 2018, 772, 719–727. [Google Scholar] [CrossRef]
  9. Chaus, A.; Sitkevich, M.; Pokorný, P.; Sahul, M.; Haršáni, M.; Babincová, P. Wear resistance and cutting performance of high-speed steel ball nose end mills related to the initial state of tool surface. Wear 2021, 472, 203711. [Google Scholar] [CrossRef]
  10. Yan, X.; Li, D. Effects of the sub-zero treatment condition on microstructure, mechanical behavior and wear resistance of W9Mo3Cr4V high speed steel. Wear 2013, 302, 854–862. [Google Scholar] [CrossRef]
  11. Xu, L.; Wei, S.; Xing, J.; Long, R. Effects of carbon content and sliding ratio on wear behavior of high-vanadium high-speed steel (HVHSS) under high-stress rolling–sliding contact. Tribol. Int. 2014, 70, 34–41. [Google Scholar] [CrossRef]
  12. Emmer, Š.; Baksa, P.; Kováčik, J. Effect of microstructure on the sonotrode properties of tool materials Ferrotitanit® WFN and steel CPM 10V®. Met. Mater. 2015, 53, 423–428. [Google Scholar] [CrossRef]
  13. Aleksić, A.; Sekulić, M.; Gostimirović, M.; Rodić, D.; Savković, B.; Antić, A. Effect of cutting parameters on cutting forces in turning of CPM 10V Steel. J. Prod. Eng. 2021, 24, 5–8. [Google Scholar] [CrossRef]
  14. Li, Y.J.; Jiang, Q.C.; Zhao, Y.G.; He, Z. Behavior of aluminium in M2 steel. Scr. Mater. 1997, 37, 173–177. [Google Scholar] [CrossRef]
  15. Myers, N.; Heaney, D. Metal injection molding (MIM) of high-speed tool steels. In Handbook of Metal Injection Molding; Woodhead Publishing: Sawston, UK, 2012; pp. 516–525. [Google Scholar] [CrossRef]
  16. Bryson, W.E. Selection of Tool Steel Grades. In Heat Treatment; Carl Hanser Verlag: Munich, Germany, 2015; pp. 191–193. [Google Scholar] [CrossRef]
  17. Yang, B.X.; He, J.Y.; Zhang, G.F.; Guo, J. Applications of vanadium in the steel industry. In Vanadium; Elsevier: Amsterdam, The Netherlands, 2021; Chapter 11; pp. 267–332. [Google Scholar]
  18. Zhou, X.F.; Yin, X.Y.; Fang, F.; Jiang, J.Q. Study on the solidification microstructure of aluminum alloyed high speed steel. Adv. Mater. Res. 2011, 217, 463–467. [Google Scholar] [CrossRef]
  19. Lin, C.W.; Hsieh, P.Y.; Chou, C.M.; Chung, C.J.; He, J.L. Femtosecond laser surface roughening and pulsed plasma polymerization duplex treatment on medical-grade stainless steel substrates for orthodontic purpose. Surf. Coat. Technol. 2021, 427, 127819. [Google Scholar] [CrossRef]
  20. Kovacı, H.; Seçer, Y. Improved tribological performance of AISI 316L stainless steel by a combined surface treatment: Surface texturing by selective laser melting and plasma nitriding. Surf. Coat. Technol. 2020, 400, 126178. [Google Scholar] [CrossRef]
  21. Sun, X.T. Material Surface Strengthening Technology; Chemical Industry Press: Beijing, China, 2005. [Google Scholar]
  22. Zhang, H.; Zou, Y.; Zou, Z.D. Effects of CeO2 on microstructure and corrosion resistance of TiC-VC reinforced Fe-based laser cladding layers. J. Rare. Earth 2014, 32, 1095–1100. [Google Scholar] [CrossRef]
  23. Li, C.; Liu, H.X.; Zhang, X.W.; Tao, X. Microstructure and property of Co-based carbide composite coating fabricated by laser cladding on 40Cr tool steel surface. China J. Lasers 2015, 42, 1103002. [Google Scholar]
  24. Yasavol, N.; Abdollah-Zadeh, A.; Ganjali, M.; Alidokht, S.A. Microstructure and mechanical behavior of pulsed laser surface melted AISID2 cold work tool steel. Appl. Surf. Sci. 2013, 265, 653–662. [Google Scholar] [CrossRef]
  25. Liu, H.X.; Dong, T.; Zhang, X.W.; Liu, Z.F.; Shi, H. Microstructure and cutting performance of WC/Co50/Al cemented carbide coated tools fabricated by laser cladding process. China J. Lasers 2017, 44, 0802002. [Google Scholar]
  26. Sohi, M.H.; Karshenas, G.; Boutorabi, S. Electron beam surface melting of as cast and austempered ductile irons. J. Mater. Process. Technol. 2004, 153, 199–202. [Google Scholar] [CrossRef]
  27. Shi, K.Y. The Study on Microstructure and Fatigue Properties of Plasma Transferred Arc (PTA) Hardening on Grey Cast Iron; Huazhong University of Science & Technology: Wuhan, China, 2012. [Google Scholar]
  28. Yan, M.; Zhu, W. Surface treatment of 45 steel by plasma-arc melting. Surf. Coat. Technol. 1997, 91, 183–191. [Google Scholar] [CrossRef]
  29. Khater, M.A.; Mostafa, A.M.; Al-Ashkar, E.A. Role of laser fluence on ionic emission characteristics from steel plasmas induced in atmospheric air. Radiat. Phys. Chem. 2021, 185, 109515. [Google Scholar] [CrossRef]
  30. Jovičević-Klug, M.; Jovičević-Klug, P.; Kranjec, T.; Podgornik, B. Cross-effect of surface finishing and deep cryogenic treatment on corrosion resistance of AISI M35 steel. J. Mater. Res. Technol. 2021, 14, 2365–2381. [Google Scholar] [CrossRef]
  31. Zou, H.; Guan, Q.F.; Zhang, Q.Y.; Dong, C.; Liang, L. Surface modification of 45# steel by high-current pulsed electron beam. J. Jilin Univ. (Eng. Technol. Ed.) 2004, 34, 127–131. [Google Scholar]
  32. Hao, S.Z.; Wu, P.S.; Zhang, X.D.; Zhou, J.X.; Qin, Y.; Dong, C. Surface modification by high current pulsed electron beam. Heat Treat. Metals 2008, 33, 77–81. [Google Scholar]
  33. Zhao, H.; Yi, Y.; Chen, Y.; Zhu, Q. Surface modification of 4Cr13 stainless steel by irradiation of high current pulsed electron beam. J. Mater. Protect. 2011, 44, 72–74. [Google Scholar]
  34. Wei, Q.Q. Effects of alloying elements and heat treatment on property of light section steel structure. Hot Work. Technol. 2014, 43, 179–181. [Google Scholar]
  35. Kwok, C.; Cheng, F.; Man, H. Microstructure and corrosion behavior of laser surface-melted high-speed steels. Surf. Coat. Technol. 2007, 202, 336–348. [Google Scholar] [CrossRef]
  36. Xiong, G.; Xie, F.W.; Yuan, Z.R.; Kang, X.Y.; He, Y.H. Microstructure and properties of carbon-free Fe-Co-Mo high speed steel coating prepared by laser cladding. Mater. Sci. Eng. Powder Metall. 2021, 26, 84–90. [Google Scholar]
  37. Rahman, N.U.; Capuano, L.; van der Meer, A.; de Rooij, M.; Matthews, D.; Walmag, G.; Sinnaeve, M.; Garcia-Junceda, A.; Castillo, M.; Römer, G. Development and characterization of multilayer laser cladded high speed steels. Addit. Manuf. 2018, 24, 76–85. [Google Scholar] [CrossRef]
  38. Rahman, N.U.; de Rooij, M.; Matthews, D.; Walmag, G.; Sinnaeve, M.; Römer, G. Wear characterization of multilayer laser cladded high speed steels. Tribol. Int. 2018, 130, 52–62. [Google Scholar] [CrossRef]
  39. Sun, G.; Wang, K.; Zhou, R.; Feng, A.; Zhang, W. Effect of different heat-treatment temperatures on the laser cladded M3:2 high-speed steel. Mater. Des. 2015, 65, 606–616. [Google Scholar] [CrossRef]
  40. Cao, H.T.; Dong, X.P.; Pan, Z.; Wu, X.W.; Huang, Q.W.; Pei, Y.T. Surface alloying of high-vanadium high-speed steel on ductile iron using plasma transferred arc technique: Microstructure and wear properties. Mater. Des. 2016, 100, 223–234. [Google Scholar] [CrossRef]
  41. Fang, Z.; Tie, M.G.; Qiang, L.; Yin, Y.; Zhang, R.; Nan, X. Effect of solution aging treatment on microstructure and properties of Fe-0.5 C-11Cr corrosion resistant alloy by laser cladding. J. Alloys Compd. 2022, 922, 166142. [Google Scholar] [CrossRef]
  42. Chen, C.Z.; Yu, H.J.; Zhou, X.L. Structure and properties of high-speed steel remelted by laser. Appl. Laser 1997, 17, 149–152. [Google Scholar]
  43. Tuo, J.H.; Chen, S.Y.; Zhou, L.; Liu, C.H.; Li, H.L. Effect of laser surface modification on microstructure and hardness of high speed steel roll. Heat Treat. Metals 2006, 31, 56–59. [Google Scholar]
  44. Li, Y.; Xiao, F.; Wang, Y.; Zhang, G.; Yao, J.; Liu, Y. M2 high speed steel irradiated by high-intensity pulsed ion beam. China J. Mater. Res. 2005, 19, 613–618. [Google Scholar]
  45. Li, Y.H.; Xing, G.H.; Li, S.Z.; Lou, C.S.; Yuan, J.W. Surface modification of M2 high-speed steel by high intense pulsed ion beam. J. Shenyang Univ. Technol. 2010, 32, 141–145. [Google Scholar]
  46. Li, S.Z.; Li, Y.H.; Xu, T.T. Surface modification of high-speed steel M2 by HCPEB. Surf. Technol. 2009, 24–26. [Google Scholar]
  47. Chen, G.Q.; Teng, X.Y.; Shu, X.; Zhang, B. Hardening effect of electron beam surface remelting on W6 steel. Trans. China Weld. Inst. 2022, 42, 1–6. [Google Scholar]
  48. Omar, S.; Plucknett, K. The influence of DED process parameters and heat-treatment cycle on the microstructure and hardness of AISI D2 tool steel. J. Manuf. Process. 2022, 81, 655–671. [Google Scholar] [CrossRef]
  49. Mei, X.X.; Ma, T.C.; Wang, X.M.; Xu, W.; Song, M. Surface modification of W6Mo5Cr4V2 high-speed steel by high-intensity pulsed ion beam. Acta. Metall. Sin. 2003, 39, 926–931. [Google Scholar]
  50. Liao, X.J.; Lu, L.; Fu, Q.F. Surface modification of M42 high speed steel by pulse detonation-plasma treatment. Heat Treat. Metals 2015, 40, 166–170. [Google Scholar]
  51. Yu, J.M.; Zhang, L.W.; Zou, J.; Fu, Q.F.; Zhou, Z.; Lu, L. Structure and properties of m2 high speed steel surface modified by pulse detonation-plasma technology. J. Mater. Protect. 2016, 49, 4–7. [Google Scholar]
  52. Shang, Q.B.; Yu, A.B.; Wei, J.L.; Wang, Y. Friction and wear properties of high speed steel surface with Ni-based WC laser cladding bumps. Appl. Laser 2015, 5, 525–529. [Google Scholar]
  53. Han, T. Different Introduction Ways of Submicron MC-Type Reinforcement by Laser Alloying; Huazhong University of Science & Technology: Wuhan, China, 2012. [Google Scholar]
  54. Bourithis, L.; Papadimitriou, G. Synthesizing a class “M” high speed steel on the surface of a plain steel using the plasma transferred arc (PTA) alloying technique: Microstructure and wear properties. Mater. Sci. Eng. A 2003, 361, 165–172. [Google Scholar] [CrossRef]
  55. Zhang, J.Q.; Dong, L.; Ju, H.; Lin, X. Micro-structure and properties of surface coating on a high speed steel by laser cladding. Trans. Mater. Heat Treat. 2016, 37, 196–200. [Google Scholar]
  56. Tang, H. Study on Microstructure and Properties of the High Alloy Content High Speed Steel Coating Produced by Laser Cladding; Anhui University of Technology: Maanshan, China, 2019. [Google Scholar]
  57. Zheng, H.B. Research on M2 Coating Prepared by Ultra-High Speed Laser Cladding; China Academy of Machinery Science and Technology Group: Beijing, China, 2021. [Google Scholar]
  58. Liu, M.; Jiang, H.; Chang, G.; Xu, Y.; Ma, F.; Xu, K. Effect of laser remelting on corrosion and wear resistance of Fe82Cr16SiB alloy coatings fabricated by extreme high-speed laser cladding. Mater. Lett. 2022, 325, 132823. [Google Scholar] [CrossRef]
  59. Chen, X. Study on Laser Cladding Modification Technology Based on W6Mo5Cr4V2 High-Speed Steel Cutter; Liaoning University of Technology: Jinzhou, China, 2019. [Google Scholar]
  60. Chen, X.; Zhang, D.X.; Sun, W.Q.; Wang, Y.C.; Zhang, J.Q. Microstructure and red hardness of WC/Co coating on M2 high-speed steel cutter surface prepared by laser cladding. Surf. Tech. 2019, 48, 236–243. [Google Scholar]
  61. Wu, M.C.; Yu, A.B.; Wei, J.L.; Chen, Q.; Sun, L.; Yuan, J. Influences of cladding materials on cracks and hardnesses of laser cladding chip breakers on high-speed steel cutting tools. China Mech. Eng. 2020, 30, 1607–1612, 1620. [Google Scholar]
  62. Cao, H.T.; Dong, X.P.; Li, W.F.; Pan, Z.; Huang, Q.W. Study on the microstructure and performance of ductile iron by PTA alloying high vanadium high-speed steel coating. Foundry 2014, 63, 637–641. [Google Scholar]
  63. Cao, H.T.; Dong, X.P.; Chen, S.Q.; Dutka, M.; Pei, Y.T. Microstructure evolutions of graded high-vanadium tool steel composite coating in-situ fabricated via atmospheric plasma beam alloying. J. Alloys Compd. 2017, 720, 169–181. [Google Scholar] [CrossRef]
  64. Cao, H.T.; Dong, X.P.; Chabok, A.; Rao, J.C.; De Hosson, Y.T.; Pei, Y. Hard-yet-tough high-vanadium hierarchical composite coating: Microstructure and mechanical properties. Mater. Sci. Eng. A 2018, 736, 87–99. [Google Scholar] [CrossRef]
  65. Wang, Y.L.; He, Y.; Hong, X.; Chen, B.; Yu, A. Friction reducing mechanism of high speed steel textured surface with Ni-based WC laser cladding stripes. Laser Optoelectron. Prog. 2018, 55, 021403. [Google Scholar] [CrossRef]
  66. Ripoll, M.R.; Ojala, N.; Katsich, C.; Totolin, V.; Tomastik, C.; Hradil, K. The role of niobium in improving toughness and corrosion resistance of high speed steel laser hardfacings. Mater. Des. 2016, 99, 509–520. [Google Scholar] [CrossRef]
  67. Liu, Z.; Fu, P.; Zhao, J.; Ji, F.; Zhang, Y.; Nagaumi, H.; Wang, X.; Zhao, Y.; Jia, P.; Li, W. Corrosion and high-temperature tribological behavior of carbon steel claddings by additive manufacturing technology. Surf. Coat. Technol. 2019, 384, 125325. [Google Scholar] [CrossRef]
Materials 15 06129 g001 550
Figure 1. Schematic of processing method: (a) High-energy beam remelting; (b) High-energy beam cladding; (c) High-energy beam alloying.
Figure 1. Schematic of processing method: (a) High-energy beam remelting; (b) High-energy beam cladding; (c) High-energy beam alloying.
Materials 15 06129 g001
Materials 15 06129 g002 550
Figure 2. SEM image of W6 HSS (a) Lamellar M2C eutectic carbide; (b) Fine flake martensite; (c) Unfused spherical MC carbide; (d) XRD results [47].
Figure 2. SEM image of W6 HSS (a) Lamellar M2C eutectic carbide; (b) Fine flake martensite; (c) Unfused spherical MC carbide; (d) XRD results [47].
Materials 15 06129 g002
Materials 15 06129 g003 550
Figure 3. Wear test results of W18Cr4V HSS [42].
Figure 3. Wear test results of W18Cr4V HSS [42].
Materials 15 06129 g003
Materials 15 06129 g004 550
Figure 4. SEM images of the surfaces of HSS (a) non-irradiated; (b) irradiated with 1 pulse; (c) irradiated with 3 pulses; (d) irradiated with 5 pulses showing the crater formation after irradiation by HIPIB [49].
Figure 4. SEM images of the surfaces of HSS (a) non-irradiated; (b) irradiated with 1 pulse; (c) irradiated with 3 pulses; (d) irradiated with 5 pulses showing the crater formation after irradiation by HIPIB [49].
Materials 15 06129 g004
Materials 15 06129 g005 550
Figure 5. The dynamic potential polarization curves of M2 HSS before and after PDT [51].
Figure 5. The dynamic potential polarization curves of M2 HSS before and after PDT [51].
Materials 15 06129 g005
Materials 15 06129 g006 550
Figure 6. Local reconstruction of M35 HSS pitting corrosion after 1 day (a) and after 7 days (b) [30].
Figure 6. Local reconstruction of M35 HSS pitting corrosion after 1 day (a) and after 7 days (b) [30].
Materials 15 06129 g006
Materials 15 06129 g007 550
Figure 7. Optical images of cross-sectional appearance and SEM images of the melting zone (MZ)of the laser-melted specimens (a,b) LSM-M2; (c,d) LSM-ASP23; (e,f) LSM-ASP30 [35].
Figure 7. Optical images of cross-sectional appearance and SEM images of the melting zone (MZ)of the laser-melted specimens (a,b) LSM-M2; (c,d) LSM-ASP23; (e,f) LSM-ASP30 [35].
Materials 15 06129 g007
Materials 15 06129 g008 550
Figure 8. (a) SEM micrograph of the alloyed zone. The former austenite grains transformed on cooling to martensite (gray) and are surrounded by globular M6C carbides and a eutectic mixture containing M2C carbides (white areas); (b) SEM showing, in detail, the microstructure of Figure 6a. Dark gray areas are former austenite grains transformed to martensite and are separated by a duplex M6C/γ and M2C/γ eutectic. Globular white particles are M6C carbides, from which the M2C carbides are radially emanating [54].
Figure 8. (a) SEM micrograph of the alloyed zone. The former austenite grains transformed on cooling to martensite (gray) and are surrounded by globular M6C carbides and a eutectic mixture containing M2C carbides (white areas); (b) SEM showing, in detail, the microstructure of Figure 6a. Dark gray areas are former austenite grains transformed to martensite and are separated by a duplex M6C/γ and M2C/γ eutectic. Globular white particles are M6C carbides, from which the M2C carbides are radially emanating [54].
Materials 15 06129 g008
Materials 15 06129 g009 550
Figure 9. TEM characterization of the C-0.65 HSS coatings after triple-tempering at 530 °C: (a,b) brightfield images; (c) dark field image; (d) the corresponding SAED pattern for (b) [56].
Figure 9. TEM characterization of the C-0.65 HSS coatings after triple-tempering at 530 °C: (a,b) brightfield images; (c) dark field image; (d) the corresponding SAED pattern for (b) [56].
Materials 15 06129 g009
Materials 15 06129 g010 550
Figure 10. Specimen cross-sectional shape: (a–c) P = 1500 W; (d–f) P = 1700 W; (g–i) P = 1900 W [57].
Figure 10. Specimen cross-sectional shape: (a–c) P = 1500 W; (d–f) P = 1700 W; (g–i) P = 1900 W [57].
Materials 15 06129 g010
Materials 15 06129 g011 550
Figure 11. BSE-SEM images showing different carbides present in the laser cladded HSS alloys with EDS images [37].
Figure 11. BSE-SEM images showing different carbides present in the laser cladded HSS alloys with EDS images [37].
Materials 15 06129 g011
Materials 15 06129 g012 550
Figure 12. SE-SEM images showing wear morphologies of different samples (200 N): (a) PTA-alloyed HVHSS coating; (b) PTA-remelted; (c) Mn13 steel; (d) DI substrate [40].
Figure 12. SE-SEM images showing wear morphologies of different samples (200 N): (a) PTA-alloyed HVHSS coating; (b) PTA-remelted; (c) Mn13 steel; (d) DI substrate [40].
Materials 15 06129 g012
Materials 15 06129 g013 550
Figure 13. Cross-sectional SEM microstructure in near surface region: (a) EHLA; (b) EHLA-LR; Wear test results: (c) Wear scar width and wear rate; (d) Wear appearance of EHLA; (e) Wear appearance of EHLA-LR; (f) Wear appearance of the substrate [58].
Figure 13. Cross-sectional SEM microstructure in near surface region: (a) EHLA; (b) EHLA-LR; Wear test results: (c) Wear scar width and wear rate; (d) Wear appearance of EHLA; (e) Wear appearance of EHLA-LR; (f) Wear appearance of the substrate [58].
Materials 15 06129 g013
Materials 15 06129 g014 550
Figure 14. SEM images of bottom region of the cladding layer of sample: (a) Cross-section structure of cladding layer; (b) Microstructure of cladding layer (A. Fe3W3C; B. W2C, a few Fe3W3C and Mo2V4C5; C. Fe3W3C, and WC; D. M6C type hard phase with Co element; E. Fe solid solution with a large amount of W and a small amount of Co, C, and other elements; F. Co6W6C) [60].
Figure 14. SEM images of bottom region of the cladding layer of sample: (a) Cross-section structure of cladding layer; (b) Microstructure of cladding layer (A. Fe3W3C; B. W2C, a few Fe3W3C and Mo2V4C5; C. Fe3W3C, and WC; D. M6C type hard phase with Co element; E. Fe solid solution with a large amount of W and a small amount of Co, C, and other elements; F. Co6W6C) [60].
Materials 15 06129 g014
Materials 15 06129 g015 550
Figure 15. Microhardness profile of HVHSS graded coating on iron substrate as a function of depth [63].
Figure 15. Microhardness profile of HVHSS graded coating on iron substrate as a function of depth [63].
Materials 15 06129 g015
Materials 15 06129 g016 550
Figure 16. (a) SEM images showing the cross-section of the HVHSS graded coating and (b) linear EDS scan along the line A–B marked in (a); Close view of the microstructure of the alloying zone (AZ) (c), melting zone (MZ) (d) and heated affected zone (HAZ) (e), respectively [64].
Figure 16. (a) SEM images showing the cross-section of the HVHSS graded coating and (b) linear EDS scan along the line A–B marked in (a); Close view of the microstructure of the alloying zone (AZ) (c), melting zone (MZ) (d) and heated affected zone (HAZ) (e), respectively [64].
Materials 15 06129 g016
Materials 15 06129 g017 550
Figure 17. (a) EDS area mapping showing TiC/V8C7 double carbides in a PTA prepared high vanadium HSS coating; (b) bright-field TEM image showing MC carbide cluster in the AZ with the crosses numbered for EDS; (c–f) related SADPs of spot 1–4, respectively, indicated by circles in (b) [64].
Figure 17. (a) EDS area mapping showing TiC/V8C7 double carbides in a PTA prepared high vanadium HSS coating; (b) bright-field TEM image showing MC carbide cluster in the AZ with the crosses numbered for EDS; (c–f) related SADPs of spot 1–4, respectively, indicated by circles in (b) [64].
Materials 15 06129 g017
Materials 15 06129 g018 550
Figure 18. Wear rate for HSS laser hardfacings tested under low-stress abrasion conditions as a function of the niobium content [66].
Figure 18. Wear rate for HSS laser hardfacings tested under low-stress abrasion conditions as a function of the niobium content [66].
Materials 15 06129 g018
Materials 15 06129 g019 550
Figure 19. SEM analyses of the corrosion layer present on the HSS laser hardfacings after potentiodynamic tests: (a,b) the corrosion layer with a porous "mud-cracked" structure; (c,d) the corrosion layer becomes more continuous and denser after adding 3 % Nb [66].
Figure 19. SEM analyses of the corrosion layer present on the HSS laser hardfacings after potentiodynamic tests: (a,b) the corrosion layer with a porous "mud-cracked" structure; (c,d) the corrosion layer becomes more continuous and denser after adding 3 % Nb [66].
Materials 15 06129 g019
Materials 15 06129 g020 550
Figure 20. (a) Nyquist curves of HSS and different carbon steel claddings; (b) phase angle of HSS and different carbon steel claddings; (c) Schematic of tested materials [67].
Figure 20. (a) Nyquist curves of HSS and different carbon steel claddings; (b) phase angle of HSS and different carbon steel claddings; (c) Schematic of tested materials [67].
Materials 15 06129 g020
Table
Table 1. The classification and trademarks of HSS [2].
Table 1. The classification and trademarks of HSS [2].
ClassificationTrademark in ChinaTrademark in AmericaTrademark in GermanISO 4957:1999
HSS-LW3Mo3Cr4V2——HS3-3-2
W3Mo3Cr4VSi———
HSSW18Cr4VT11.3355HS18-0-1
W2Mo8Cr4VM11.3327HS1-8-1
W2Mo9Cr4V2M71.3348HS2-9-2
W6Mo5Cr4V2M21.3343HS6-5-2
CW6Mo5Cr4V2CM2 HS6-5-2C
W6Mo6Cr4V2M3:11.3350HS6-6-2
W9Mo3Cr4V———
HSS-EW6Mo6Cr4V3——HS6-5-3
CW6Mo6Cr4V3——HS6-5-3C
W6Mo6Cr4V4——HS6-5-4
W6Mo6Cr4V2Al———
W12Cr4V5Co5T151.3202—
W6Mo5Cr4V2Co5M351.3243HS6-5-2-5
W6Mo5Cr4V3Co8M3:2 + Co1.3244HS6-5-3-8
W7Mo4Cr4V2Co5M41——
W2Mo9Cr4VCo8M421.3247HS2-9-1-8
W10Mo4Cr4V3Co10M481.3207HS10-4-3-10
CPM10V
W12Cr4V4MoEV4
W6Mo5Cr4V2CM36
W9Cr4V5Co3
W6Mo5Cr4V2AlM2-Al
W12Cr4V3Mo3Co5Si
W6Mo5Cr4V5SiNbAl
W10Mo4Cr4V3Al
Table
Table 2. Hardness enhancement effects of different intensification processes.
Table 2. Hardness enhancement effects of different intensification processes.
SubstratesCoating Materials PowderIntensification ProcessHardnessHardness
Enhancement		Refs.
W18Cr4V HSS—laser remelting950 HV150 HV[23]
AISID2 tool steel—laser remelting69 HRC9 HRC[24]
M2 HSS—plasma beam remelting—150 HV[25,26]
plasma beam remelting—115 HV[27]
electron beam remelting800 HV517 HV[28]
carbon steelM2 HSStransfer plasma arc759 HV200—[30]
M2 HSS966T high hardness wirelaser cladding60 HRC—[31]
Q235 steelM2 HSSlaser cladding813 HV0.5—[32]
9Cr2Mo steelM2 HSSlaser cladding800 HV—[33]
40Cr steelFe-Cr-Mo-W-V HSSlaser cladding900~950 HV0.2—[34]
42CrMo4 HSSFe-Cr-Mo-W-V HSSlaser cladding843 HV—[35]
M2 HSSWC/Colaser surface alloying1311 HV—[36,37]
M2 HSSM2/WC-12Colaser surface alloying907 HV—[38]
ductile cast ironHVHSSplasma beam surface alloying957 HV0.2757 HV0.2[39,40,41]
Publisher’s Note: MDPI stays neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Share and Cite

MDPI and ACS Style

Li, S.; Dong, X.; Guo, S.; Liu, X.; Cao, H. Status and Perspective of High-Energy Beam Surface Strengthening: High-Speed Steel. Materials 2022, 15, 6129. https://doi.org/10.3390/ma15176129

AMA Style

Li S, Dong X, Guo S, Liu X, Cao H. Status and Perspective of High-Energy Beam Surface Strengthening: High-Speed Steel. Materials. 2022; 15(17):6129. https://doi.org/10.3390/ma15176129

Chicago/Turabian Style

Li, Shang, Xuanpu Dong, Shuren Guo, Xinwang Liu, and Huatang Cao. 2022. "Status and Perspective of High-Energy Beam Surface Strengthening: High-Speed Steel" Materials 15, no. 17: 6129. https://doi.org/10.3390/ma15176129

Note that from the first issue of 2016, this journal uses article numbers instead of page numbers. See further details here.

Article Metrics

Back to TopTop