FeCrCuTiV high-entropy alloy powder for laser melting deposition manufacturing and preparation method thereof

Abstract

Provided is a FeCrCuTiV high-entropy alloy powder for laser melting deposition manufacturing and a preparation method thereof, in percent by weight, the composition of the high-entropy alloy powder is: chromium 17-20%; copper 22-25%; titanium 16-19%; vanadium 17-20%; and ferrum 19-22%, wherein by utilizing the solid solution effect of alloying elements such as Ti, V and Cu of the high-entropy alloy, it can effectively alleviate the differences in thermal expansion coefficient, melting point, elastic modulus, etc. of the tungsten/steel or tungsten/copper heterogeneous interface, can reduce the residual stress level at the heterogeneous interface during the laser melting deposition manufacturing process and avoid the precipitation of Laves phase, and can meet the manufacturing requirements of tungsten/steel and tungsten/copper heterogeneous components for fusion reactors.

Claims

1. A preparation method of a FeCrCuTiV high-entropy alloy powder for laser melting deposition manufacturing, the preparation method comprising: (1) preparing raw materials consisting of: chromium 17-20%; copper 22-25%; titanium 16-19%; vanadium 17-20%; ferrum 19-22%, in percent by weight; (2) adding the raw materials to an induction furnace, to be electrified heated for melting to form an alloy solution, wherein the adding the raw materials includes adding a part of the raw materials into the induction furnace for melting to form the alloy solution and then adding rest of the raw materials to the alloy solution successively as supplement materials, further wherein, when adding the supplement materials into the induction furnace, a temperature inside the induction furnace is controlled between 1500° C.-1550° C.; discharging the alloy solution after confirming composition of the alloy solution in the induction furnace to be consistent with a proportion of the raw materials, wherein a discharging temperature of the alloy solution is 1450° C.-1500° C.; (3) vacuum atomizing the alloy solution obtained in Step (2) to form alloy powder, wherein an atomizing medium is argon, and an atomizing pressure is 2-10 MPa; (4) drying the alloy powder obtained in Step (3), wherein a drying temperature is 200-250° C.; and (5) screening the alloy powder obtained in Step (4) by a screening machine to screen out the alloy powder with a required particle size range.

2. The preparation method according to claim 1, w herein in percent by weight, the raw materials consisting ofcomprising chromium 19.2%, copper 22.3%, titanium 17.7%, vanadium 19.0%, and ferrum 21.8%.

3. The preparation method according to claim 1, w herein in percent by weight, the raw materials consisting ofcomprising chromium 17.8%, copper 24.8%, titanium 18.7%, vanadium 19.4%, and ferrum 19.3%.

4. The preparation method according to claim 1, wherein a particle size of the FeCrCuTiV high-entropy alloy powder obtained in Step (5) is 100 mesh-350 mesh.

Description

BRIEF DESCRIPTION

(1) Some of the embodiments will be described in detail, with references to the following Figures, wherein like designations denote like members, wherein:

(2) FIG. 1 shows an X-ray diffraction pattern of FeCrCuTiV high-entropy alloys obtained in Embodiment 1;

(3) FIG. 2 shows an X-ray diffraction pattern of FeCrCuTiV high-entropy alloys obtained in Embodiment 2;

(4) FIG. 3 is a metallurgical structure diagram of FeCrCuTiV high-entropy alloys obtained in Embodiment 1;

(5) FIG. 4 is a metallurgical structure diagram of FeCrCuTiV high-entropy alloys obtained in Embodiment 2;

(6) FIG. 5 is a scanning electron micrograph of FeCrCuTiV high-entropy alloys obtained in Embodiment 1; and

(7) FIG. 6 is a scanning electron micrograph of FeCrCuTiV high-entropy alloys obtained in Embodiment 1.

DETAILED DESCRIPTION

(8) In the following, the technical solution of the present disclosure is further set forth.

(9) The present disclosure provides a FeCrCuTiV high-entropy alloy powder for laser melting deposition manufacturing, in percent by weight, the composition of the high-entropy alloy powder is: chromium 17-20%; copper 22-25%; titanium 16-19%; vanadium 17-20%; rest is ferrum, which accounts for 19-22%.

(10) The functions of each element in the FeCrCuTiV high-entropy alloy powder are as follows:

(11) Chromium: to ensure corrosion resistance and high temperature oxidation resistance, and to improve mechanical properties;

(12) Copper: to improve strength and toughness;

(13) Titanium: to improve strength and toughness, and to improve hydrogen corrosion resistance under high temperature and high pressure;

(14) Vanadium: to improve mechanical properties and high-temperature creep properties.

(15) By utilizing the solid solution effect of alloying elements such as Ti, V and Cu of the high-entropy alloy, it can effectively alleviate the differences in thermal expansion coefficient, melting point, elastic modulus, etc. of the tungsten/steel or tungsten/copper heterogeneous interface, can reduce the residual stress level at the heterogeneous interface during the laser melting deposition manufacturing process and avoid the precipitation of Laves phase, and can meet the manufacturing requirements of tungsten/steel and tungsten/copper heterogeneous components for fusion reactors.

(16) The present disclosure further provides a preparation method for the above-mentioned FeCrCuTiV high-entropy alloy powder for laser melting deposition manufacturing, comprising the following steps: preparing raw materials.fwdarw.melting.fwdarw.vacuum atomization.fwdarw.drying.fwdarw.screening, which is specifically as follows:

(17) (1) Preparing raw materials:

(18) Taking metal ferrum, metal chromium, metal copper, metal titanium and metal vanadium as raw materials, and preparing them according to a target composition;

(19) (2) Melting:

(20) (2.1) Adding the prepared metal ferrum, metal chromium, metal copper, metal titanium, and metal vanadium to a medium frequency induction furnace, and to be electrified heated to melt;

(21) In this melting step, a part of the prepared raw materials is added to the medium frequency induction furnace for melting first, and rest of the prepared raw materials are added as a supplement to the alloy solution successively, and when adding the supplement, temperature inside the medium frequency induction furnace is controlled between 1500° C.-1550° C.;

(22) (2.2) Discharging after adjusting the composition in the medium frequency induction furnace to be qualified, and discharging temperature of the alloy solution is 1450° C.-1500° C.;

(23) (3) Vacuum atomization:

(24) Atomizing the alloy solution obtained in Step (2), wherein the atomizing medium is argon, and atomizing pressure is 2-10 MPa;

(25) (4) Drying:

(26) Drying the alloy powder obtained by atomization in Step (3), and in this step, a far infrared dryer is used, and drying temperature is 200-250° C.;

(27) (5) Screening:

(28) Screening the alloy powder obtained by drying in Step (4) by a screening machine to screen out the alloy powder with particle size range of 100 mesh-350 mesh as final product, that is, the desired FeCrCuTiV high-entropy alloy powder.

(29) The raw materials used in the present disclosure are not limited in the source, and are all commercial products.

(30) Adopting Standard GB/T223 “Methods for chemical analysis of ferrum, steel and alloy”, the composition of FeCrCuTiV high-entropy alloy powder prepared by the above preparation method is tested, and the test result is, in percent by weight, ferrum 19-22%, chromium 17-20%, copper 22-25%, titanium 16-19%, and vanadium 17-20%.

(31) After cooling the above FeCrCuTiV high-entropy alloy powder to room temperature, a laser additive manufacturing method is used to manufacture parts with complex flow channel structures, the steps are as follows:

(32) (1) Three-dimensional modeling, slicing using an image slice software, and at the same time, designing a forming path with a path planning software;

(33) (2) Selecting different process parameters, analyzing the impact of the process on the structure and properties, proposing the best process parameters, and printing the parts according to the pre-established forming path;

(34) (3) Performing post-treatments such as surface cleaning and stress relief annealing to obtain high-quality parts.

(35) The following are the preferred embodiments:

Embodiment 1

(36) The raw materials were prepared according to the following proportions, in percent by weight, comprising: chromium 19.2%, copper 22.3%, titanium 17.7%, vanadium 19.0%, and ferrum 21.8%.

(37) The prepared metal ferrum, metal chromium, metal copper, metal titanium, and metal vanadium were added into a medium frequency induction furnace, and were electrified heated to melt, and the temperature inside the medium frequency induction furnace was controlled at 1520° C. It was discharged after adjusting the composition in the furnace to be qualified, and the discharging temperature of the alloy solution was 1460° C.

(38) The alloy solution was atomized to product an alloy powder, the atomizing medium was argon, and the atomizing pressure was 4 MPa;

(39) A far infrared dryer was used to dry the alloy powder after atomization treatment, and the drying temperature was 210° C. A screening machine was used to screen out the alloy powder with a particle size range of 100 mesh-350 mesh as final product.

(40) After cooling the above final product to room temperature, a laser additive manufacturing method was used to manufacture parts with complex flow channel structures.

Embodiment 2

(41) The raw materials were prepared according to the following proportions, in percent by weight, comprising: chromium 17.8%, copper 24.8%, titanium 18.7%, vanadium 19.4%, and ferrum 19.3%.

(42) The prepared metal ferrum, metal chromium, metal copper, metal titanium, and metal vanadium were added into a medium frequency induction furnace, and were electrified heated to melt, and the temperature inside the medium frequency induction furnace was controlled at 1520° C. It was discharged after adjusting the composition in the furnace to be qualified, and the discharging temperature of the alloy solution was 1460° C.

(43) The alloy solution was atomized to product an alloy powder, the atomizing medium was argon, and the atomizing pressure was 4 MPa;

(44) A far infrared dryer was used to dry the alloy powder after atomization treatment, and the drying temperature was 210° C. A screening machine was used to screen out the alloy powder with a particle size range of 100 mesh-350 mesh as final product.

(45) After cooling the above final product to room temperature, a laser additive manufacturing method was used to manufacture parts with complex flow channel structures.

(46) The Vickers hardness test was performed on the FeCrCuTiV high-entropy alloy powders obtained in the above two embodiments, wherein the Vickers hardness test had a guaranteed time of 10 s and a test force of 200 g, and the test results are as follows:

(47) TABLE-US-00002 Vickers Hardness Test Results Measurement 1/ Measurement 2/ Measurement 3/ Measurement/ HV0.2 HV0.2 HV0.2 HV0.2 Embodiment 1 32.8 30.2 30.4 31.1 FeCrCuTiV-1 Embodiment 2 37.6 37.2 38.3 37.7 FeCrCuTiV-2

(48) The above Vickers hardness test results show that the hardness of the FeCrCuTiV high-entropy alloy obtained in the two embodiments is at a high level, and the Vickers hardness of the FeCrCuTiV high-entropy alloy with low copper content in Embodiment 1 is significantly lower than that of the FeCrCuTiV high-entropy alloy with high copper content in Embodiment 2.

(49) The tensile test was performed on the FeCrCuTiV high-entropy alloy powders obtained in the above two embodiments, and the test results are as follows:

(50) TABLE-US-00003 Tensile Test Results Tensile Strength/Mpa Break Elongation/% Embodiment 1 610.3 13.2 FeCrCuTiV-1 Embodiment 2 654.2 10.9 FeCrCuTiV-2

(51) The above tensile test results show that the FeCrCuTiV high-entropy alloy obtained in the two embodiments are excellent in mechanical properties, and the tensile strength of the FeCrCuTiV high-entropy alloy with low copper content in Embodiment 1 is lower than that of the FeCrCuTiV high-entropy alloy with high copper content in Embodiment 2, while the break elongation of Embodiment 1 is greater than that of Embodiment 2.

(52) FIG. 1 is X-ray diffraction pattern of FeCrCuTiV high-entropy alloy obtained in Embodiment 1, and FIG. 2 is X-ray diffraction pattern of FeCrCuTiV high-entropy alloy obtained in Embodiment 2, and it can be seen from the figures that the alloy is a simple FCC+BCC structure, and no other complex phases are generated in the alloy.

(53) FIG. 3 is metallurgical structure diagram of FeCrCuTiV high-entropy alloy obtained in Embodiment 1; and FIG. 4 is metallurgical structure diagram of FeCrCuTiV high-entropy alloy obtained in Embodiment 2, FIG. 5 is scanning electron micrograph of FeCrCuTiV high-entropy alloy obtained in Embodiment 1; and FIG. 6 is scanning electron micrograph of FeCrCuTiV high-entropy alloy obtained in Embodiment 2, and it can be seen from the figures that the FeCrCuTiV high-entropy alloy has large grains.

(54) From the above, it can be seen that the FeCrCuTiV high-entropy alloy powder for laser melting deposition manufacturing provided by the present disclosure, has good comprehensive properties, which can reduce the residual stress level at the heterogeneous interface during the laser melting deposition manufacturing process and avoid the precipitation of Laves phase, and can meet the manufacturing requirements of tungsten/steel and tungsten/copper heterogeneous components for fusion reactors.

(55) The embodiments described above are only for illustrating the technical concepts and features of the present disclosure, and are intended to make those skilled in the art being able to understand the present disclosure and thereby implement it, and should not be concluded to limit the protective scope of this disclosure. Any equivalent variations or modifications according to the spirit of the present disclosure should be covered by the protective scope of the present disclosure.

(56) Although the present invention has been disclosed in the form of preferred embodiments and variations thereon, it will be understood that numerous additional modifications and variations could be made thereto without departing from the scope of the invention.

(57) For the sake of clarity, it is to be understood that the use of ‘a’ or ‘an’ throughout this application does not exclude a plurality, and ‘comprising’ does not exclude other steps or elements.