WO2021051308A1 - Procédé et élément de fabrication additive - Google Patents

Procédé et élément de fabrication additive Download PDF

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Publication number
WO2021051308A1
WO2021051308A1 PCT/CN2019/106446 CN2019106446W WO2021051308A1 WO 2021051308 A1 WO2021051308 A1 WO 2021051308A1 CN 2019106446 W CN2019106446 W CN 2019106446W WO 2021051308 A1 WO2021051308 A1 WO 2021051308A1
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WO
WIPO (PCT)
Prior art keywords
additive manufacturing
temperature
time
component
hours
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PCT/CN2019/106446
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English (en)
Chinese (zh)
Inventor
周忠娇
李长鹏
陈国锋
Original Assignee
西门子股份公司
西门子（中国）有限公司
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Priority to PCT/CN2019/106446 priority Critical patent/WO2021051308A1/fr
Publication of WO2021051308A1 publication Critical patent/WO2021051308A1/fr

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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
    • 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
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C64/00—Additive manufacturing, i.e. manufacturing of three-dimensional [3D] objects by additive deposition, additive agglomeration or additive layering, e.g. by 3D printing, stereolithography or selective laser sintering
    • B29C64/10—Processes of additive manufacturing
    • B29C64/141—Processes of additive manufacturing using only solid materials
    • B29C64/153—Processes of additive manufacturing using only solid materials using layers of powder being selectively joined, e.g. by selective laser sintering or melting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C64/00—Additive manufacturing, i.e. manufacturing of three-dimensional [3D] objects by additive deposition, additive agglomeration or additive layering, e.g. by 3D printing, stereolithography or selective laser sintering
    • B29C64/30—Auxiliary operations or equipment
    • B29C64/379—Handling of additively manufactured objects, e.g. using robots

Definitions

  • the present invention relates to the field of additive manufacturing, in particular to methods and components of additive manufacturing.
  • Additive Manufacturing is one of the important 3D printing technologies.
  • the additive manufacturing process can quickly produce pre-designed CAD models, and can produce components with complex structures in a short period of time.
  • SLM Selected Laser Melting
  • the Selected Laser Melting (SLM) process is a type of additive manufacturing (Additive manufacturing) technology, which can quickly manufacture parts that are the same as the CAD model by means of laser sintering.
  • the selective laser melting process has been widely used. Different from the traditional material removal mechanism, additive manufacturing is based on the completely opposite material incremental manufacturing philosophy. Among them, selective laser melting uses high-power lasers to melt metal powder, and inputs layer by layer through 3D CAD. The components/components can be built up to the ground so that components with complex internal channels can be successfully manufactured.
  • additively manufactured materials show strong tensile strength and similar strength to manufactured components.
  • creep and fatigue test conditions need to be considered.
  • most of the additively manufactured components show a shorter stress failure life than traditionally manufactured components, even after the heat treatment process, and the voids at the boundary between the linear dendrites can cause early failure.
  • the first aspect of the present invention provides an additive manufacturing method, wherein, after performing additive manufacturing, the following steps are performed on the additive manufacturing element: heating the additive manufacturing element to a first temperature and holding it for a first time, and then setting the first temperature It is lowered to the second temperature and maintained for the second time, and finally the aging process is performed on the component to the third time.
  • the value range of the first temperature is 980°C-1065°C, and the value range of the first time is 30 minutes to 1.5 hours.
  • the value range of the second temperature is related to the precipitation temperature of the delta phase of the material of the element.
  • the precipitation temperature of the phase ranges from 700° C. to 1000° C.
  • the value range for the second time ranges from 3.5 hours to 4 hours and 4 hours.
  • the value range of the third temperature is 850°C-950°C.
  • first temperature, the first time, the second temperature, the second time, the third temperature, and the third time are related to an additive manufacturing process and printing parameters.
  • the additive manufacturing step is performed in a selective laser melting device.
  • the second aspect of the present invention provides an additive manufacturing element manufactured according to the additive manufacturing method of the first aspect of the present invention.
  • the present invention can retain the columnar crystal structure of the element material and transform the grain boundaries of the columnar crystals into a zigzag shape, so that even if a crack occurs, the crack propagation speed will not be so fast, so it can slow down the advantage of the crack propagation speed, and Improve component life by changing the shape of the grain boundary.
  • Figure 1 is a schematic diagram of selective laser melting equipment
  • Figure 2 is a schematic diagram of the creep strain comparison curves of components manufactured by several different processes
  • FIG. 3 is a schematic diagram of the crystal structure of the component after the solid solution and aging process is performed on the additive manufacturing component;
  • Figure 4 is a comparison diagram of low-cycle fatigue life after different heat treatments are performed on additive manufacturing components
  • FIG. 5 is a temperature curve diagram of heating, cooling and aging procedures of an additive manufacturing method according to a specific embodiment of the present invention.
  • Fig. 6 is a comparison diagram of the grain boundary morphology of the prior art and the present invention.
  • Curve S1 refers to the component creep strain after the solid solution plus double aging process is performed after the additive manufacturing process. Specifically, after first solution treatment at 980°C for 1 hour, then air cooling (AC, Air cooling) treatment, plus two-stage aging (718°C for 8 hours), and finally furnace cooling (FC) to 621°C , Keep warm for 10h.
  • Curve S2 is the creep strain of the printed element without heat treatment after the additive manufacturing is completed.
  • Curve S3 represents the creep strain of the component after performing direct aging after the additive manufacturing process, then directly aging at 718°C for 8 hours, and finally furnace cooling (FC) to 621°C and holding for 10 hours.
  • Curve S4 represents the component made in forging. As shown in Figure 2, it can be seen that compared to the meta-software made by forging, whether it is a component after the solution and aging process after the additive manufacturing process, or the component after the additive manufacturing process after the aging process, its creep performance is the same. Not ideal. It should be noted that the materials targeted by the above process are all In718, which is a precipitation hardening nickel-chromium-iron alloy containing niobium and molybdenum.
  • FIG. 3 is a schematic diagram of the component microstructure after the solution and aging process is performed on the additive manufacturing component.
  • the crystal structure of the component after the solution and aging process is performed on the additive manufacturing component is columnar crystal 200, columnar
  • the anisotropy of the crystal 200 is relatively high, because the crystal grain size is in two directions. Specifically, the length direction (Z direction) of the columnar crystal is relatively long, and although it has a relatively high creep strength, it also causes its fatigue life to be relatively short. At the same time, the horizontal width of the columnar crystals is relatively narrow, although the fatigue performance is high, the creep performance is also relatively poor, so it is difficult to control the columnar crystals; in addition, the scattered crystals (fine grains) around the columnar crystals will further reduce the forming Piece creep performance.
  • the reference numeral 300 indicates the sample fracture of the component after the solution and aging process is performed on the additive manufacturing component.
  • the reference numeral 300a indicates the small hole between the crystal grains, and the reference numeral 300b indicates the sliding surface.
  • Reference numeral 400 indicates an enlarged view of 300. As shown in the figure, after the sample fractured, it was found that the crack occurred at the relatively straight grain boundary and spread along the grain boundary. This is what we don't want to see.
  • the ideal heating process after additive manufacturing includes the final stage with mainly uniform and non-directional recrystallized grain structure, and there is no residual structure of the structure.
  • an ideal heating process needs to have the following two characteristics. The first is to retain the excellent mechanical properties in one direction, and the second is to reduce the crack growth rate and improve the mechanical properties in other directions.
  • Figure 4 is a comparison diagram of the low-cycle fatigue life of the components after different heat treatments are performed on the additive-manufactured components.
  • the samples are manufactured based on the nickel-chromium-iron alloy in718.
  • the histogram C1 and the histogram C2 belong to the first heating process
  • the histograms C3 and C4 belong to the second heating process
  • the histograms C1 and C3 are the sample loading direction (the direction of force) parallel to the printing direction (mechanical performance test)
  • the histograms C2 and C4 are both the sample loading direction (the direction of force) perpendicular to the printing direction (mechanical performance test).
  • the sample after the first heating process is performed, the sample exhibits a significantly anisotropic columnar crystal structure, the columnar crystals are parallel to the element formation direction, and show the highest average lifespan compared to the lateral columnar material.
  • early cracks originate from straight grain boundaries, resulting in short low-cycle fatigue life in parallel directions.
  • the mechanical anisotropy After the second heating process is performed, the mechanical anisotropy has almost disappeared.
  • the samples are parallel to the component formation direction, and show similar low-cycle fatigue life compared to those perpendicular to the component formation direction, but whether it is parallel or perpendicular to the component formation direction.
  • the components manufactured in the component forming direction all have a lower lifetime than the components that perform the first heating process and are perpendicular to the component forming direction.
  • the sample loading direction (the direction of force) perpendicular to the printing direction shows a longer life
  • the crystal grains also show strong anisotropy, which means that the sample is perpendicular to the printing direction and retains the columnar crystal structure.
  • the performance of the best low-cycle fatigue life is the best low-cycle fatigue life.
  • the first heat treatment is solid solution plus double aging.
  • solid solution is performed to 980°C to 1h
  • air cooling plus double aging is performed at 760°C to 10h
  • the furnace is cooled to 650°C to 2h, and finally kept at 650°C to 8h.
  • the second heat treatment is homogenization+double aging (HA, homogenization+double aging), in which the temperature of the homogenization treatment is 1065°C, the time of the homogenization treatment is 1h, and then air cooling plus bipolar aging to 760°C to 10h ,
  • the furnace is finally cooled to 650°C for 2h, and finally kept at 650°C for 2h.
  • the present invention proposes an additive manufacturing method.
  • the additive manufacturing is performed first to obtain an additive manufacturing component, wherein the additive manufacturing step is performed in a selective laser melting device.
  • FIG. 1 is a schematic diagram of a selective laser melting device.
  • the selective laser melting device 100 includes a laser source 110, a mirror scanner 120, a prism 130, a powder feeding cylinder 140, a forming cylinder 150 and a recovery cylinder 160.
  • the laser source 110 is arranged above the selective laser melting device 100 and serves as a heating source for the metal powder, that is, the metal powder is melted for 3D printing.
  • first piston (not shown) that can move up and down at the lower part of the powder feeding cylinder 140.
  • a spare metal powder is placed in the cavity space above the first piston of the powder feeding cylinder 140, and it follows the movement of the first piston.
  • the metal powder is sent from the powder feeding cylinder 140 to the forming cylinder 150 by moving up and down.
  • a 3D printed part placement table 154 is provided in the forming cylinder 150, a 3D printed part C is clamped above the placement table 154, and a second piston 152 is fixed below the placement table 154, among which, the second piston 152 and the placement table 154 Vertical setting. During the 3D printing process, the second piston 152 moves from top to bottom to form a printing space in the molding cylinder 220.
  • the laser source 110 for laser scanning should be set above the forming cylinder 150 of the selective laser melting equipment.
  • the mirror scanner 120 adjusts the position of the laser by adjusting the angle of a prism 130, and determines which area of the laser melts the metal by adjusting the prism 130. powder.
  • the powder feeding cylinder 140 further includes a roller (not shown), and the metal powder P is stacked on the upper surface of the first piston, and the first piston vertically moves from bottom to top to transfer the metal powder to the upper part of the powder feeding cylinder 140.
  • the selective laser melting device 100 further includes a roller, and the 3D printing powder can be laid on the forming cylinder 220 by the rolling of the roller. The roller may roll on the metal powder P to send the metal powder P to the forming cylinder 150.
  • the laser scanning is continuously performed on the metal powder to decompose the metal powder into a powder matrix, and the laser scanning of the powder matrix is continued until the powder matrix is sintered from the bottom to the top into a print with a preset shape.
  • the selective laser melting device 100 further includes a recovery cylinder 160, and the recovery cylinder 160 is used to recover the used metal powder in the forming cylinder 150.
  • the following steps are performed on the additive manufacturing component: heating the additive manufacturing component to a first temperature and holding it for a first time, then reducing the first temperature to a second temperature and holding it for a second time, and finally The component executes the aging procedure to the third time.
  • the solid line S1 represents the temperature curve of the heating, cooling and aging procedures of the present invention
  • the dashed line S2 represents the temperature curve of the heat treatment and aging procedures of the prior art, where the abscissa is time and the ordinate is temperature.
  • the prior art additive manufacturing heat treatment procedure needs to perform a heating step and then heat preservation, and an aging step is performed after the temperature drops.
  • the additive manufacturing component is heated to 750 and left for two hours, and then the aging step is performed.
  • the additive manufacturing component is first heated to a first temperature and maintained for a first time, specifically, the first temperature T1 is reached at the first time t1, and the first temperature T1 is maintained for the first time, Among them, the first time is t2-t1.
  • the first temperature T1 is then reduced to the second temperature T2 for a second time, specifically, the temperature is lowered from the second time t2 to the third time t3, and is reduced to the third time t3
  • the second temperature is T2, and the second temperature is maintained for a second time, wherein the second time is t4-t3.
  • an aging procedure (aging) is performed on the component to a third time, where the third time is t6-t5, and the temperature of the aging procedure is T3.
  • the grain boundary shape obtained by the heat treatment and aging procedure of the prior art is 500
  • the grain boundary obtained by the heat treatment procedure of additive manufacturing provided by the present invention is zigzag 600.
  • the additive manufacturing method and device provided by the present invention can form a zigzag shape at the grain boundary by adjusting the heat treatment process to control the grain boundary geometric structure. Also for the nickel-chromium-iron alloy In718 material, the present invention first performs a heating step, and then performs a cooling step, reducing the temperature to T at a rate of less than 12°C/min to promote the precipitation of the ⁇ phase, which will be used for the sawtooth crystal The formation of the world.
  • the serrated grain boundary will improve the crack propagation resistance, thus improving the mechanical properties including creep characteristics and the low-cycle fatigue life.
  • the low-cycle fatigue life is quite low for different super heat-resistant stainless steels.
  • the microstructure of In718 superalloy is mainly composed of ⁇ matrix, dispersed strengthening phases ⁇ ′ and ⁇ ′′, phases, and a small amount of NbC.
  • There is segregation in the microstructure of In718 alloy manufactured by additive which rises to High temperature can make the element distribution as uniform as possible through diffusion and eliminate segregation; and further cooling can promote the precipitation of ⁇ phase at the grain boundary, and by pinning the grain boundary, restraining the movement of the grain boundary, thereby forming a sawtooth grain boundary.
  • the value range of the first temperature is 980°C-1065°C
  • the value range of the first time is 30 minutes to 1.5 hours, and preferably the first time is 1 hour.
  • the value range of the second temperature is related to the precipitation temperature of the delta phase of the material of the element.
  • the precipitation temperature of the ⁇ phase ranges from 700°C to 1000°C
  • the value range for the second time ranges from 3.5 hours to 4 hours, preferably the second The time is 4 hours.
  • the value range of the third temperature is 850°C-950°C, preferably the third time is 760°C.
  • first temperature, the first time, the second temperature, the second time, the third temperature, and the third time are related to an additive manufacturing process and printing parameters.
  • the second aspect of the present invention provides an additive manufacturing element, wherein the additive manufacturing element is manufactured according to the additive manufacturing method according to the first aspect of the present invention.
  • the present invention can retain the columnar crystal structure of the element material and transform the grain boundary of the columnar crystal into a zigzag shape, so that even if a crack occurs, the crack propagation speed will not be so fast, so it can slow down the advantage of the crack propagation speed, and Improve component life by changing the shape of the grain boundary.

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  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Chemical & Material Sciences (AREA)
  • Manufacturing & Machinery (AREA)
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  • Mechanical Engineering (AREA)
  • Optics & Photonics (AREA)
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Abstract

L'invention concerne un procédé et un élément de fabrication additive. Après réalisation de la fabrication additive, les étapes suivantes sont exécutées pour l'élément de fabrication additive et consistent à: chauffer l'élément de fabrication additive à une première température et maintenir celle-ci pendant une première période de temps, puis réduire la première température à une seconde température et maintenir celle-ci pendant une deuxième période de temps, et enfin exécuter un processus de vieillissement sur l'élément pendant une troisième période de temps.
PCT/CN2019/106446 2019-09-18 2019-09-18 Procédé et élément de fabrication additive WO2021051308A1 (fr)

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PCT/CN2019/106446 WO2021051308A1 (fr) 2019-09-18 2019-09-18 Procédé et élément de fabrication additive

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PCT/CN2019/106446 WO2021051308A1 (fr) 2019-09-18 2019-09-18 Procédé et élément de fabrication additive

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Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107815627A (zh) * 2017-03-25 2018-03-20 山东建筑大学 一种基于激光选区熔化的3D打印Inconel718镍基合金的热处理工艺方法
CN109848422A (zh) * 2019-02-25 2019-06-07 南昌航空大学 选区激光熔化成形gh4169合金的热处理方法
CN110079752A (zh) * 2019-05-07 2019-08-02 西安交通大学 抑制3d打印或焊接的单晶高温合金再结晶的热处理方法

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107815627A (zh) * 2017-03-25 2018-03-20 山东建筑大学 一种基于激光选区熔化的3D打印Inconel718镍基合金的热处理工艺方法
CN109848422A (zh) * 2019-02-25 2019-06-07 南昌航空大学 选区激光熔化成形gh4169合金的热处理方法
CN110079752A (zh) * 2019-05-07 2019-08-02 西安交通大学 抑制3d打印或焊接的单晶高温合金再结晶的热处理方法

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