CN110280764A - A kind of Maraging steel and preparation method thereof based on SLM molded part - Google Patents

A kind of Maraging steel and preparation method thereof based on SLM molded part Download PDF

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Publication number
CN110280764A
CN110280764A CN201910663071.2A CN201910663071A CN110280764A CN 110280764 A CN110280764 A CN 110280764A CN 201910663071 A CN201910663071 A CN 201910663071A CN 110280764 A CN110280764 A CN 110280764A
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molded part
slm
slm molded
maraging steel
preparation
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杨立军
郑航
李俊
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Shaanxi University of Science and Technology
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Shaanxi University of Science and Technology
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/20—Direct sintering or melting
    • B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/60—Treatment of workpieces or articles after build-up
    • B22F10/64—Treatment of workpieces or articles after build-up by thermal means
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/60—Treatment of workpieces or articles after build-up
    • B22F10/66—Treatment of workpieces or articles after build-up by mechanical means
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y10/00—Processes of additive manufacturing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y70/00—Materials specially adapted for additive manufacturing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/30—Process control
    • B22F10/32—Process control of the atmosphere, e.g. composition or pressure in a building chamber
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/30—Process control
    • B22F10/36—Process control of energy beam parameters
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/30—Process control
    • B22F10/36—Process control of energy beam parameters
    • B22F10/366—Scanning parameters, e.g. hatch distance or scanning strategy
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • B22F2003/247—Removing material: carving, cleaning, grinding, hobbing, honing, lapping, polishing, milling, shaving, skiving, turning the surface
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • B22F2003/248—Thermal after-treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Abstract

The Maraging steel and preparation method thereof based on SLM molded part that the invention discloses a kind of obtains SLM molded part firstly, forming using the powder of Maraging steel as raw material using SLM；Then, SLM molded part is surface-treated, obtains fine and close SLM molded part；It is handled finally, carrying out solution treatment, ageing treatment or direct aging to fine and close SLM molded part, obtains the Maraging steel of selective laser melting (SLM) molding part；The present invention is handled by using solution treatment, ageing treatment or direct aging and is heat-treated to SLM molded part, effectively increases the mechanical strength of SLM molded part and the toughness of SLM；The scope of application of SLM molded part is expanded, industrial design manufacture demand is preferably met；The microhardness of Maraging steel based on SLM molded part is 400-430HV, tensile strength 900-1000Mpa.

Description

A kind of Maraging steel and preparation method thereof based on SLM molded part
Technical field
The invention belongs to Steel material technical field, in particular to a kind of Maraging steel based on SLM molded part and its Preparation method.
Background technique
Maraging steel is that a kind of superhigh intensity, high tenacity are rigid, since the advent of the world its be widely used in aerospace, essence The numerous areas such as close gear and precision die.The high reason of martensite ag(e)ing hardness of steel is the Ni of nano-scale3(Mo, Ti) and Fe2Mo intermetallic compound particle precipitates during heat treatment.Above-mentioned particle will be by inhibiting the mobility of dislocation significant Enhance microhardness and intensity.Martensite ag(e)ing steel making handling ease, many advantages such as welding performance is excellent are better than other Super-high strength steel, in all material developed now, it is the highest steel grade of obdurability.
Selective laser melting (SLM) molding part (SLM molded part) be produced by using the layer-by-layer method of laser beam it is relatively highly dense The metal parts of degree, in aerospace, automobile, medical treatment and industrial circle have broad application prospects；SLM formed body is layer-by-layer When molding, molten bath is very small, solidification rate very fast about 104-106, molten bath is very high.It is raw due to lacking enough crystal grain For a long time, intercrystalline is obtained away from the equiaxed crystal and columnar crystal structure less than 1 μm, and the mechanical property of SLM molded part depends on In structural state, the requirements of the national standard of forging is not achieved in the deposited components performance of SLM molded part under normal circumstances, often By heat treatment process, change its structural state, and then changes its service performance.
Due to the molding special microstructure and properties of SLM, using traditional heat treatment mode, the SLM molded part of acquisition The microstructure ingredient uniformity of Maraging steel and microscopic segregation, with the cast member being heat-treated using same way There are larger differences for the performance of Maraging steel.
Summary of the invention
In view of the deficiency of the prior art, the present invention provide a kind of Maraging steel based on SLM molded part and Preparation method, to solve poor, smaller scope of application, nothing based on SLM molded part martensite ag(e)ing Steel Properties in the prior art Method meets the technical issues of industrial design demand.
To achieve the above object, the technical solution of the present invention is as follows:
The present invention provides a kind of preparation methods of Maraging steel based on SLM molded part, comprising the following steps:
Step 1, using the powder of Maraging steel as raw material, formed using SLM, obtain SLM molded part；
Step 2 is surface-treated the SLM molded part in step 1；
Step 3, in step 2 by surface treatment after SLM molded part carry out solution treatment, ageing treatment or it is direct when Effect processing, obtains the Maraging steel based on SLM molded part.
Further, by mass percentage, the martensite ag(e)ing powdered steel, including Ni:18.2%-20.0%, Co: 10%-13%, Mo:4%-9%, Ti:0.5%-1.0%, Al:0.1%-0.3%, C:0.2%-0.5% and Fe: surplus.
Further, by mass percentage, the martensite ag(e)ing powdered steel, including Ni:18.2%, Co:9%, Mo: 5.3%, Ti:0.8%, Al:0.1%, C:0.2% and Fe: surplus.
Further, the powder of Maraging steel uses 18Ni-300 comminuted steel shot in step 1,18Ni-300 comminuted steel shot comminuted steel shot Spherical particle diameters are 15-45 μm；18Ni-300 comminuted steel shot is prepared using gas atomization.
Further, it in step 1, is formed using SLM, during preparing SLM molded part, using in protective gas atmosphere Under enclosing；Laser scanning speed is 400-600mm/s, laser power 160-180W；Every layer of powdering with a thickness of 0.03-0.05mm, Laser scanning pitch is 0.05-0.07mm.
Further, SLM molded part is surface-treated using blasting craft in step 2.
Further, in step 3, when carrying out solution treatment to surface treated SLM molded part, specifically: true Under Altitude or protective gas atmosphere, surface treated SLM molded part is warming up to 920-960 DEG C in 1h-2h, and 1.5-2.5h is kept the temperature under the conditions of 920-960 DEG C, it is air-cooled later to arrive room temperature.
Further, in step 3, when carrying out ageing treatment to surface treated SLM molded part, specifically: true Under Altitude or protective gas atmosphere, surface treated SLM molded part is warming up to 900-920 DEG C in 1h-2h；And 2-2.5h is kept the temperature under the conditions of 900-920 DEG C；Then it is cooled to 540-560 DEG C with 10-15 DEG C/min, and keeps the temperature 4-6h, later It is air-cooled to arrive room temperature.
Further, in step 3, when carrying out direct aging processing to surface treated SLM molded part, specifically: Under vacuum environment or protective gas atmosphere, surface treated SLM molded part is warming up to 400- in 0.6h-0.8h 450℃；And 4-6h is kept the temperature under the conditions of 400-450 DEG C, it is air-cooled later to arrive room temperature.
The present invention also provides a kind of Maraging steel based on SLM molded part, the horse based on SLM molded part The microhardness of family name's body aged steel is 400-712HV, tensile strength 900-2120Mpa.
Compared with prior art, the beneficial effects of the present invention are:
The present invention provides a kind of preparation methods of Maraging steel based on SLM molded part, at solid solution Reason, ageing treatment or direct aging processing are heat-treated SLM molded part；Heat temperature raising is carried out using to SLM molded part, is promoted It is full of gap into SLM crystal grain, microelement realizes uniformly diffusion, it is ensured that internal residual stress disappears, and effectively increases SLM molding The mechanical strength of part and the toughness of SLM；The scope of application of SLM molded part is expanded, industrial design manufacture demand is preferably met.
Further, martensite failure powdered steel uses the combining form of Ni, Co, Mo, Ti, Al, C and Fe, phosphorus content Lower, the intensity of martensite increases, and by the way that Ni is added, can obtain single martensite after ensure that the quenching of SLM molded part；Its It is secondary, hardening constituent Ni is formed when Ni acts on Mo3Mo, Ti, Al, Mo etc. are microelement, realize induration；The horse Family name's body fails powdered steel with good cold and hot working performance, and SLM molded part has high-intensitive, high tenacity.
Further, martensite failure powdered steel uses 18Ni-300 steel, and 18Ni-300 steel is typical martensite ag(e)ing Steel has excellent physical and mechanical property, corrosion resistance, weldability and heat treatment characteristic, utilizes SLM forming technique, Neng Goucheng Structure is complicated for type, precision size, the part and mold of service life length, using the molding SLM molded part of 18Ni-300 steel, different Under heat treatment, the performance that SLM molded part shows also difference is greatly enlarged the application prospect of Maraging steel.
Further, when carrying out forming parts using SLM technology, the molded part consistency of manufacture can reach 99%, compare With traditional casting technique, it can be achieved that manufacturing complicated part, production, and do not need mold.
Further, since SLM molded part has fritting powder and floating powder is attached on surface, by using blasting craft pair The surface of SLM molded part is handled；Impact and shear action by sand-blasting abrasive to SLM forming part surface, it is ensured that SLM The floating powder of surface of shaped parts falls off, it is ensured that SLM surface of shaped parts roughness reduces, and improves the fatigue resistance of SLM molded part.
When further, by using solution treatment to SLM molded part, the temperature of SLM molded part is increased to 920-960 DEG C, sufficiently grow its crystal grain full of gap, microelement is spread in entire body, and internal residual stress substantially completely disappears, Austenite grain growth is converted into bigger martensite lath, and without white crystal boundary, crystal grain is uniformly distributed, and the number of die of dislocation subtracts Few, microhardness is reduced compared to ageing treatment, and stretching hardness reduces, and extensibility increases, and is suitable for production gear matrix.
Further, by using ageing treatment to SLM molded part, so that most of austenite heating is converted into geneva Body, microelement are uniformly spread, lath martensite fast-growth；To when being cooled to 540-560 DEG C, 4-6h is persistently kept the temperature, because More energy are obtained, martensite continues to increase, and boundary is may be seen indistinctly, and obtaining part microhardness is 670-712HV, stretches strong Degree is 1022-1200MPa；Its intensity is high, rigidity is suitable for well gear tooth, precision machine tool.
When further, by being handled using direct aging SLM molded part, due to the limitation of temperature, the intracorporal Austria of machine Family name's body can not be converted into martensite, the micro other elements combination of austenite and precipitating, and the dislocation crystal grain of generation increases, whole table Now increase for tensile strength, microhardness increases, and extensibility reduces, and molded part has very high mechanical performance, microhardness For 653-700HV, ultimate tensile strength 2000-2120MPa.
The present invention also provides a kind of Maraging steel based on SLM molded part, the Maraging steel of SLM molded part Microhardness be 400-712HV, tensile strength 900-2120Mpa；The SLM molded part obtained using different heat treatment mode Maraging steel, can be applied to different work condition environments, expand the scope of application of SLM molded part.
Detailed description of the invention
Fig. 1 is the surface microscopic figure of SLM molded part in the present invention；
Fig. 2 is the sintering temperature change curve of three kinds of SLM molded part heretofore described heat treatment；
Fig. 3 is the metallographic structure figure of the Maraging steel of SLM molded part obtained in embodiment 1 in the present invention；
Fig. 4 is the metallographic structure figure of the Maraging steel of SLM molded part obtained in embodiment 2 in the present invention；
Fig. 5 is the metallographic structure figure of the Maraging steel of SLM molded part obtained in embodiment 3 in the present invention.
Specific embodiment
Understand in order to make the object, technical scheme and advantages of the embodiment of the invention clearer, with reference to the accompanying drawing to this hair Bright embodiment is described in further details.Here, the illustrative embodiments of the present invention and their descriptions are used to explain the present invention, but simultaneously It is not as a limitation of the invention.
The present invention provides a kind of preparation methods of Maraging steel based on SLM molded part, comprising the following steps:
Step 1, using the powder of Maraging steel as raw material, formed using SLM, obtain SLM molded part；
Step 2 is surface-treated the SLM molded part in step 1；
Step 3 carries out solution treatment, ageing treatment or direct aging to SLM molded part surface treated in step 2 Processing, obtains the Maraging steel of selective laser melting (SLM) molding part.
Embodiment 1
A kind of preparation method of the Maraging steel based on SLM molded part, comprising the following steps:
Step 1, using the powder of Maraging steel as raw material, formed using SLM, obtain SLM molded part；
When preparing SLM molded part using SLM forming technique, before printing starts, when enough martensite is added in powder cylinder Imitate powdered steel；Since the moulding cylinder and powder cylinder of common 3D printer are equal in magnitude, martensite ag(e)ing powdered steel is added Amount be not less than two times of forming part height；Before printing starts, inert protective gas is passed through into printing storehouse, it is ensured that printing storehouse Interior oxygen content is lower than 0.05%, then starts printing shaping；In entire printing shaping process, the flow of inert protective gas is big In 1.2Lpm；Specific print parameters are as follows: laser scanning speed 400-600mm/s, laser power 160-180W；Every layer of powdering With a thickness of 0.03-0.05mm, laser scanning pitch 0.05-0.07mm；The SLM surface of shaped parts being prepared is smooth, is not easy Buckling deformation occurs, part consistency is measured by Archimedes's drainage, experiments have shown that the print parameters can make part Consistency reach 99.17%, have reached the technical level of hot investment casting part.
Martensite ag(e)ing powdered steel, as mass fraction, including Ni:18.0%-20.0%, Co:10%-13%, Mo: 4%-9%, Ti:0.5%-1.0%, Al:0.1%-0.3%, C:0.2%-0.5% and Fe: surplus；
Preferably, martensite ag(e)ing powdered steel, as mass fraction, including Ni:18.2%, Co:9%, Mo:5.3%, Ti:0.8%, Al:0.1%, C:0.2% and Fe: surplus.
Preferably, martensite ag(e)ing powdered steel uses the rigid powder of 18Ni-300 of gas atomization manufacture, spherical particle diameters About 15 μm -45 μm.
Step 2 is surface-treated the SLM molded part in step 1；
Since SLM surface of shaped parts is there are unmelted powder and floating powder, using blasting craft carry out surface treatment promote SLM at Airfoil surface does not melt powder and floating powder falls off；Blasting craft specifically: use compressed air for power, sprayed with the high speed of formation Material spray high speed is ejected into SLM surface of shaped parts to be processed by beam, since material spray makees the impact of SLM surface of shaped parts and cutting With, make SLM surface of shaped parts do not melt powder and floating powder falls off, Part Surface Roughness reduce, improve the antifatigue of workpiece Property；Wherein, material spray uses quartz sand, and the partial size of quartz sand is 0.2-2.0mm, blasting pressure 0.7-1MPa；Blasting treatment is complete Surface roughness at rear SLM molded part is 1.6-3.2 μm.
Step 3 carries out solution treatment, solution treatment to SLM molded part surface treated in step 2 specifically: Under vacuum environment or protective gas atmosphere, surface treated SLM molded part is warming up to 920-960 DEG C in 1h-2h, And 1.5-2.5h is kept the temperature under the conditions of 920-960 DEG C, it is air-cooled later to arrive room temperature；Obtain the Maraging steel of SLM molded part.
Attached drawing 1 gives the microcosmic surface figure for the fine and close SLM molded part being prepared in embodiment 1, can from attached drawing 1 To find out, using SLM forming technique, obtained SLM surface of shaped parts is smooth, shows ripples along laser printing direction Line, overlap joint is good between single track, the defects of burning stomata does not occur.
Attached drawing 3 gives in embodiment 1 and obtains the Maraging steel of SLM molded part by solution treatment, from attached drawing 3 As can be seen that SLM molded part, after solution treatment, crystal grain is sufficiently grown full of gap, and microelement is spread in entire machine Body, internal residual stress substantially completely disappear, and austenite grain growth is converted into bigger martensite lath, the number of die of dislocation It reduces, without white crystal boundary, crystal grain is uniformly distributed, and microhardness is reduced compared to ageing treatment, and stretching hardness reduces, and extensibility increases Add.
The microhardness of the Maraging steel of SLM molded part and tensile strength obtained in embodiment 1 are decreased obviously, Microhardness is 400-430HV, tensile strength 900-1000Mpa, the Maraging steel tool of the SLM molded part obtained at this time There is high yield strength, tensile property is improved, and is suitable for gear matrix etc..
As shown in Fig. 2, hot place is carried out to SLM molded part using solution treatment+air-cooled processing mode in embodiment 1 It manages, ε, ω, Fe successively occurs in the rising in heat treatment process with temperature from 572-600 DEG C to 872-920 DEG C2Mo and Ni3 (Ti, Mo)；When temperature is at 670 DEG C, there is α phase martensite to γ phase austenite, by BCC- body cube center to FCC- The phase transformation at face cube center；The rigid aging range of available SLM martensite ag(e)ing is 500-670 DEG C；At solid solution The raising of temperature is managed, γ phase austenite is gradually decreased at 840 DEG C is converted into the full martensitic matrix of α phase, solution temperature 840-900 ℃；Consider that the sample microsegregation of SLM part is obvious, the diffusion of microelement needs higher temperature between crystal grain, it is ensured that Gu Molten treatment effect is obvious, and therefore, the temperature setting of solution treatment is 920-960 DEG C by the present invention, keeps the temperature 1.5-2.5h.
Embodiment 2
Embodiment 2 and the preparation principle of embodiment 1 are essentially identical, the difference is that process in the step 3 of embodiment 2 It is surface-treated SLM molded part and carries out ageing treatment, obtain the Maraging steel of SLM molded part；Ageing treatment specifically: true Under Altitude or protective gas atmosphere, surface treated SLM molded part is warming up to 900-920 DEG C in 1h-2h；And 2-2.5h is kept the temperature under the conditions of 900-920 DEG C；Then it is cooled to 540-560 DEG C with 10-15 DEG C/min, and keeps the temperature 4-6h, later It is air-cooled to arrive room temperature.
The rigid microhardness of the martensite ag(e)ing of SLM molded part obtained in embodiment 2 is 670-712HV, tensile strength For 1022-1200Mpa；The Maraging steel of SLM molded part microhardness with higher and tensile strength have better Engineer application potentiality.
As shown in Fig. 2, in embodiment 2 using for ageing treatment+final air-cooled, when the temperature of ageing treatment is 780 DEG C when, it can be observed that austenite grain boundary and white particle.With the increase of temperature and soaking time, melt rail boundary is gradually Dissolution.Microstructure is made of lath martensite in sample；When temperature reach 540-560 DEG C of soaking time reach 4-6 it is small when, plate Martensite disappears and is replaced by white and dark tissue, the elimination of austenite in Maraging steel.
Attached drawing 4 gives in embodiment 2 and obtains the Maraging steel of SLM molded part by solution treatment, from attached drawing 4 As can be seen that fusing rail boundary all disappears when temperature reaches 840 DEG C；So that most of austenite heating is converted into horse Family name's body, microelement are uniformly spread, lath martensite fast-growth, to when being cooled to 540 DEG C, 4h are persistently kept the temperature, because obtaining More energy, martensite continue to increase, and boundary is may be seen indistinctly.
Embodiment 3
Embodiment 3 and the preparation principle of embodiment 1 are essentially identical, the difference is that in the step 3 of embodiment 3, to warp When SLM molded part after crossing surface treatment carries out direct aging processing, the Maraging steel of SLM molded part is obtained；When direct Effect processing specifically: under vacuum environment or protective gas atmosphere, by surface treated SLM molded part in 0.6h- 400-450 DEG C is warming up in 0.8h；And 4-6h is kept the temperature under the conditions of 400-450 DEG C, it is air-cooled later to arrive room temperature.
The Maraging steel of SLM molded part obtained in embodiment 3 has very high mechanical performance, and microhardness is The Maraging steel of 653-700HV, ultimate strength 2000-2120MPa, obtained SLM molded part are suitable for gear tooth, essence Close lathe etc..
As shown in Fig. 2, heat is carried out to fine and close SLM molded part using direct aging processing+air-cooled mode in embodiment 3 It handles, in heat treatment process in the microscopic structure of SLM molded part, α phase content is that the content of 93.8%, γ phase is 6.2%；? After 400-450 DEG C of directly heat preservation 6-8 is small, γ phase content increases to 6.9%, α phase content and accordingly reduces.With the liter of aging temp The content of height, γ phase gradually increases, and aging temp promotes the transformation of austenite.When temperature rises to 520-560 DEG C, γ phase Content increases to 17.9%.
Attached drawing 5, which gives, to be handled to obtain the Maraging steel of SLM molded part by direct aging in embodiment 3, from attached In Fig. 5 as can be seen that due to temperature limitation, the intracorporal austenite of machine can not be converted into martensite, austenite and precipitating it is micro- It measures other elements to combine, the dislocation crystal grain of generation increases, and overall performance is tensile strength increase, and microhardness increases, extensibility It reduces, white crystal boundary boundary is mainly Mo and Ti element, since low temperature cannot be completely dissolved, is sunk during direct aging processing Product forms discontinuous intermetallic phase, the hardness and tensile strength of the matrix that these intermetallic phases greatly improve.
The present invention provides a kind of preparation method of Maraging steel based on SLM molded part, by solution treatment, when Effect processing or direct aging processing mode, not only further increase the mechanical strength of SLM forming part, but also can also improve molding The toughness of part expands the scope of application of SLM molded part, preferably meets the needs of industrial design manufacture.
The rigid preparation method of martensite ag(e)ing of the present invention based on SLM molded part, it is microcosmic due to SLM molded part Metallographic ingredient is very different with conventional cast and machined part, so, the rigid aging range of SLM martensite ag(e)ing is not Together, solid solubility temperature is different, if first will cause the waste of energy, and second cannot be most with heat treatment mode traditional at present Good part performance.Three kinds of heat treatment modes of the present invention are based on many experiments gained, mainly for SLM molded part The rigid performance of martensite ag(e)ing probe into, obtain the heat treatment process of SLM forming part.
Martensite ag(e)ing powdered steel uses 18Ni-300 comminuted steel shot in the present invention, is manufactured by gas atomization, and appearance is in Spherical, diameter range is in normal distribution between 15 μm -45 μm；The powder is formed under selective laser melting process and is set The part of meter is passed through argon gas protection in entire forming process.The microscopic structure of the deposited of SLM molded part, group in the present invention It knits mainly by being formed in the coarse column crystal of epitaxial growth, single column crystal is differed through several layers of or even tens layers.
SLM forming technique is the process quickly solidified, and the solidification in molten bath is since solid phase substrate to liquid phase molten bath It carries out, preceding layer solidification layer becomes next layer of solid phase substrate, and closer to the position of contoured bottom, temperature gradient is bigger, heat It will scatter and disappear along towards solidification matrix direction, to make the column crystal of selective laser fusing forming that typical epitaxial growth feature be presented. SLM forms possessed this epitaxial growth characteristic, but also the molding microstructure of SLM is largely by the crystalline substance of substrate Body orientation is influenced.With the passage of laser beam, the heat transfer direction of molten metal is also perpendicularly to surrounding perpendicular to solidification leading edge Solidification layer.The phenomenon that macrostructure's presentation black and white alternating growth is due to caused by the crystalline orientation difference in tissue.
Three kinds of different heat treatment methods of the invention, so that the microstructure of SLM molded part produces great influence；It helps In the surface stress and internal stress of eliminating SLM molded part；So that alloy trace element is further uniformly in metallographic structure, it is brilliant Grain miniaturization, comprehensive performance improve；For the particularity of SLM molded part, three kinds of heat treatment modes proposed by the present invention are obtained The different Maraging steel of three kinds of performances, can meet the tendency of in different work condition environments, expand the molding use scope of SLM.
The above is only presently preferred embodiments of the present invention, is not intended to limit the invention in any way, it is all according to the present invention Technical spirit any simple modification to the above embodiments, change and equivalent structural changes, still fall within skill of the present invention In the protection scope of art scheme.

Claims (10)

1. a kind of preparation method of the Maraging steel based on SLM molded part, which comprises the following steps:
Step 1, using the powder of Maraging steel as raw material, formed using SLM, obtain SLM molded part；
Step 2 is surface-treated the SLM molded part in step 1；
Step 3 carries out at solution treatment, ageing treatment or direct aging the SLM molded part in step 2 after surface treatment Reason, obtains the Maraging steel based on SLM molded part.
2. a kind of preparation method of Maraging steel based on SLM molded part according to claim 1, feature exist In, by mass percentage, the martensite ag(e)ing powdered steel, including Ni:18.2%-20.0%, Co:10%-13%, Mo: 4%-9%, Ti:0.5%-1.0%, Al:0.1%-0.3%, C:0.2%-0.5% and Fe: surplus.
3. a kind of preparation method of Maraging steel based on SLM molded part according to claim 1, feature exist In, by mass percentage, the martensite ag(e)ing powdered steel, including Ni:18.2%, Co:9%, Mo:5.3%, Ti: 0.8%, Al:0.1%, C:0.2% and Fe: surplus.
4. a kind of preparation method of Maraging steel based on SLM molded part according to claim 1, feature exist In the powder of Maraging steel uses 18Ni-300 comminuted steel shot in step 1, and the spherical particle diameters of 18Ni-300 comminuted steel shot comminuted steel shot are 15-45μm；18Ni-300 comminuted steel shot is prepared using gas atomization.
5. a kind of preparation method of Maraging steel based on SLM molded part according to claim 1, feature exist In, in step 1, formed using SLM, prepare SLM molded part during, using under protective gas atmosphere；Laser scanning Speed is 400-600mm/s, laser power 160-180W；Every layer of powdering be with a thickness of 0.03-0.05mm, laser scanning pitch 0.05-0.07mm。
6. a kind of preparation method of Maraging steel based on SLM molded part according to claim 1, feature exist In SLM molded part is surface-treated using blasting craft in step 2.
7. a kind of preparation method of Maraging steel based on SLM molded part according to claim 1, feature exist In, in step 3, when carrying out solution treatment to surface treated SLM molded part, specifically: in vacuum environment or protectiveness Under atmosphere, surface treated SLM molded part is warming up to 920-960 DEG C in 1h-2h, and in 920-960 DEG C of item 1.5-2.5h is kept the temperature under part, it is air-cooled later to arrive room temperature.
8. a kind of preparation method of Maraging steel based on SLM molded part according to claim 1, feature exist In, in step 3, when carrying out ageing treatment to surface treated SLM molded part, specifically: in vacuum environment or protectiveness Under atmosphere, surface treated SLM molded part is warming up to 900-920 DEG C in 1h-2h；And in 900-920 DEG C of item 2-2.5h is kept the temperature under part；Then it is cooled to 540-560 DEG C with 10-15 DEG C/min, and keeps the temperature 4-6h, it is air-cooled later to arrive room temperature.
9. a kind of preparation method of Maraging steel based on SLM molded part according to claim 1, feature exist In, in step 3, when carrying out direct aging processing to surface treated SLM molded part, specifically: in vacuum environment or guarantor Under shield property atmosphere, surface treated SLM molded part is warming up to 400-450 DEG C in 0.6h-0.8h；And in 400- 4-6h is kept the temperature under the conditions of 450 DEG C, it is air-cooled later to arrive room temperature.
10. a kind of Maraging steel based on SLM molded part, which is characterized in that using described in claim 1-9 any one The preparation method of Maraging steel based on SLM molded part a kind of be prepared；The geneva based on SLM molded part The microhardness of body aged steel is 400-712HV, tensile strength 900-2120Mpa.
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CN113477928A (en) * 2021-07-06 2021-10-08 西安建筑科技大学 Preparation method of high-strength and high-toughness martensitic precipitation hardening stainless steel
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CN115305413A (en) * 2022-08-12 2022-11-08 合肥亚明汽车部件有限公司 3D printing insert for gearbox die-casting die and preparation process thereof
CN116275011A (en) * 2023-05-19 2023-06-23 清华大学 Powder for additive manufacturing, ultra-high strength and toughness steel, and preparation method and application thereof
CN116275011B (en) * 2023-05-19 2023-08-15 清华大学 Powder for additive manufacturing, ultra-high strength and toughness steel, and preparation method and application thereof

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