CN114589314A - Preparation method of porous metal material with secondary porous structure - Google Patents
Preparation method of porous metal material with secondary porous structure Download PDFInfo
- Publication number
- CN114589314A CN114589314A CN202210224259.9A CN202210224259A CN114589314A CN 114589314 A CN114589314 A CN 114589314A CN 202210224259 A CN202210224259 A CN 202210224259A CN 114589314 A CN114589314 A CN 114589314A
- Authority
- CN
- China
- Prior art keywords
- metal
- porous
- porous structure
- metal material
- preparing
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 239000007769 metal material Substances 0.000 title claims abstract description 32
- 238000002360 preparation method Methods 0.000 title claims abstract description 16
- 229910052751 metal Inorganic materials 0.000 claims abstract description 46
- 239000002184 metal Substances 0.000 claims abstract description 46
- 239000011812 mixed powder Substances 0.000 claims abstract description 10
- 239000003792 electrolyte Substances 0.000 claims abstract description 9
- 238000002156 mixing Methods 0.000 claims abstract description 9
- 238000006243 chemical reaction Methods 0.000 claims abstract description 3
- 239000000843 powder Substances 0.000 claims description 36
- 238000000034 method Methods 0.000 claims description 34
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 claims description 30
- 229910052715 tantalum Inorganic materials 0.000 claims description 22
- 238000000498 ball milling Methods 0.000 claims description 15
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 14
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 14
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 14
- 239000010410 layer Substances 0.000 claims description 12
- 239000002253 acid Substances 0.000 claims description 11
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 11
- 239000000758 substrate Substances 0.000 claims description 11
- 229910052802 copper Inorganic materials 0.000 claims description 10
- 239000010949 copper Substances 0.000 claims description 10
- 229910052758 niobium Inorganic materials 0.000 claims description 10
- 239000010955 niobium Substances 0.000 claims description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 8
- 229910052719 titanium Inorganic materials 0.000 claims description 8
- 239000010936 titanium Substances 0.000 claims description 8
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 7
- 229910052759 nickel Inorganic materials 0.000 claims description 7
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 claims description 6
- 239000000463 material Substances 0.000 claims description 6
- 229910052709 silver Inorganic materials 0.000 claims description 6
- 239000004332 silver Substances 0.000 claims description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 5
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 239000011651 chromium Substances 0.000 claims description 5
- 238000003892 spreading Methods 0.000 claims description 5
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 claims description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims description 4
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 4
- 229910017052 cobalt Inorganic materials 0.000 claims description 4
- 239000010941 cobalt Substances 0.000 claims description 4
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 4
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 claims description 4
- 229910052737 gold Inorganic materials 0.000 claims description 4
- 239000010931 gold Substances 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 239000011133 lead Substances 0.000 claims description 4
- 229910017604 nitric acid Inorganic materials 0.000 claims description 4
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 claims description 4
- 239000011135 tin Substances 0.000 claims description 4
- 229910052718 tin Inorganic materials 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 4
- 239000011701 zinc Substances 0.000 claims description 4
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 2
- 229910052749 magnesium Inorganic materials 0.000 claims description 2
- 239000011777 magnesium Substances 0.000 claims description 2
- 229910052697 platinum Inorganic materials 0.000 claims description 2
- 239000002356 single layer Substances 0.000 claims description 2
- 230000008018 melting Effects 0.000 abstract description 14
- 238000002844 melting Methods 0.000 abstract description 14
- 238000005516 engineering process Methods 0.000 abstract description 5
- 238000004220 aggregation Methods 0.000 abstract description 3
- 230000002776 aggregation Effects 0.000 abstract description 3
- 238000004891 communication Methods 0.000 abstract description 3
- 238000009792 diffusion process Methods 0.000 abstract description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 14
- 239000011148 porous material Substances 0.000 description 13
- 239000002245 particle Substances 0.000 description 12
- 238000010146 3D printing Methods 0.000 description 10
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 10
- 239000003518 caustics Substances 0.000 description 10
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 9
- 210000000988 bone and bone Anatomy 0.000 description 9
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 9
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 8
- 238000004140 cleaning Methods 0.000 description 8
- 238000001035 drying Methods 0.000 description 8
- 239000001301 oxygen Substances 0.000 description 8
- 229910052760 oxygen Inorganic materials 0.000 description 8
- 229910052786 argon Inorganic materials 0.000 description 7
- 238000005520 cutting process Methods 0.000 description 7
- 230000003647 oxidation Effects 0.000 description 7
- 238000007254 oxidation reaction Methods 0.000 description 7
- 239000000243 solution Substances 0.000 description 7
- 239000002131 composite material Substances 0.000 description 6
- 238000007639 printing Methods 0.000 description 6
- 238000012876 topography Methods 0.000 description 6
- 229910003460 diamond Inorganic materials 0.000 description 5
- 239000010432 diamond Substances 0.000 description 5
- 238000007648 laser printing Methods 0.000 description 5
- 239000011259 mixed solution Substances 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 3
- 239000007943 implant Substances 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 230000001276 controlling effect Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 230000010354 integration Effects 0.000 description 2
- 239000011229 interlayer Substances 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 230000001105 regulatory effect Effects 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- RFDFPOGXFHHCII-UHFFFAOYSA-N [Cu].[Nb] Chemical compound [Cu].[Nb] RFDFPOGXFHHCII-UHFFFAOYSA-N 0.000 description 1
- JRBRVDCKNXZZGH-UHFFFAOYSA-N alumane;copper Chemical compound [AlH3].[Cu] JRBRVDCKNXZZGH-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000012620 biological material Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- HBCZDZWFGVSUDJ-UHFFFAOYSA-N chromium tantalum Chemical compound [Cr].[Ta] HBCZDZWFGVSUDJ-UHFFFAOYSA-N 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000000151 deposition Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000006056 electrooxidation reaction Methods 0.000 description 1
- 238000005187 foaming Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 230000035876 healing Effects 0.000 description 1
- 238000002513 implantation Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 229910001338 liquidmetal Inorganic materials 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000001465 metallisation Methods 0.000 description 1
- VMJRMGHWUWFWOB-UHFFFAOYSA-N nickel tantalum Chemical compound [Ni].[Ta] VMJRMGHWUWFWOB-UHFFFAOYSA-N 0.000 description 1
- 229910001000 nickel titanium Inorganic materials 0.000 description 1
- HLXZNVUGXRDIFK-UHFFFAOYSA-N nickel titanium Chemical compound [Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ti].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni].[Ni] HLXZNVUGXRDIFK-UHFFFAOYSA-N 0.000 description 1
- 230000000399 orthopedic effect Effects 0.000 description 1
- 238000010883 osseointegration Methods 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 239000003870 refractory metal Substances 0.000 description 1
- 238000007789 sealing Methods 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000004544 sputter deposition Methods 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- VSSLEOGOUUKTNN-UHFFFAOYSA-N tantalum titanium Chemical compound [Ti].[Ta] VSSLEOGOUUKTNN-UHFFFAOYSA-N 0.000 description 1
- 210000001519 tissue Anatomy 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Images
Classifications
-
- 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
- B22F10/30—Process control
- B22F10/38—Process control to achieve specific product aspects, e.g. surface smoothness, density, porosity or hollow structures
-
- 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
- B22F10/62—Treatment of workpieces or articles after build-up by chemical 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
- B22F3/10—Sintering only
- B22F3/11—Making porous workpieces or articles
- B22F3/1103—Making porous workpieces or articles with particular physical characteristics
-
- 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
- B22F3/10—Sintering only
- B22F3/11—Making porous workpieces or articles
- B22F3/1143—Making porous workpieces or articles involving an oxidation, reduction or reaction step
-
- 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
- B33Y40/00—Auxiliary operations or equipment, e.g. for material handling
- B33Y40/20—Post-treatment, e.g. curing, coating or polishing
-
- 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
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25F—PROCESSES FOR THE ELECTROLYTIC REMOVAL OF MATERIALS FROM OBJECTS; APPARATUS THEREFOR
- C25F3/00—Electrolytic etching or polishing
- C25F3/02—Etching
-
- 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
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/10—Energy storage using batteries
-
- 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
Landscapes
- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Mechanical Engineering (AREA)
- Electrochemistry (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- General Chemical & Material Sciences (AREA)
- Automation & Control Theory (AREA)
- Physics & Mathematics (AREA)
- Plasma & Fusion (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention relates to a preparation method of a porous metal material with a secondary porous structure, which comprises the following steps: mixing the metal A and the metal B to obtain mixed powder, forming the mixed powder through laser region selection to obtain a blank body with a primary porous structure, placing the blank body in an electrolyte, and performing dealloying reaction to obtain a porous metal material with a secondary porous structure; the electrode potential of the component with the lowest electrode potential in the metal A is larger than that of the component with the highest electrode potential in the metal B. The preparation method comprises the steps of firstly preparing a primary porous structure with a specific morphology by utilizing a selective laser melting technology, then corroding relatively active metal in a forming structure by utilizing dealloying, and forming a nano porous structure with a three-dimensional communication network by using the residual inert elements in a surface diffusion or aggregation mode to finally obtain the porous metal material with a secondary porous structure.
Description
Technical Field
The invention relates to a preparation method of a porous metal material with a secondary porous structure, belonging to the technical field of porous metal material preparation.
Background
The orthopedic biomaterial has undergone rapid development in the past century, the design of the implant more meets the biomechanical requirements of human bodies, the material selection is more diversified, and the implant material with bioactivity brought by tissue engineering research and the like are provided. These advances have led clinicians to have more options in the face of complex cases and stable metals (tantalum, niobium, zirconium, etc.) have become more and more widely used, but as biomedical materials, traditional metallic materials still have problems with bonding at the metal prosthesis-bone interface and stress shielding.
The problem of metal prosthesis-bone interface bonding is particularly prominent in artificial joint replacement. The stability of the biotype artificial joint is obtained by the tight press fit between the prosthesis and the bone bed in the early period of implantation, and the long-term stability is mainly obtained by the osseointegration between the prosthesis and the bone interface. The patient's age, the state of the bone bed, the stability of the prosthesis during press-fitting, the surrounding stress conditions, etc. all affect the healing of the bone interface of the prosthesis, but the material and surface treatment of the prosthesis itself are more critical. In order to make the bone interface of the prosthesis obtain better bone integration, in recent years, porous metal is applied to the manufacture of joint prosthesis, the most widely applied is porous tantalum, and the research of Bobny on porous tantalum implants shows that the tantalum has good bone integration capability A plant. The porous metals currently used in the clinic include titanium, crude titanium alloys, and nitinol, with porous tantalum being the most studied. The microstructure of the porous tantalum is arranged in a dodecahedron shape, forms criss-cross grids and micropores distributed throughout the whole body, is similar to the structure of human cancellous bone, and is beneficial to the growth of bone tissues.
However, many conventional methods are not suitable for preparing porous tantalum due to the extremely high melting point temperature (2996 ℃) and the easy oxidation property of tantalum itself. At present, the trabecular metal multi-hole group of Zimmer company has complex preparation process and can not be produced by a uniform die, so that the price is very high, and the trabecular metal multi-hole group can be widely used clinically, and the selective laser melting has unique advantages in preparing refractory metal porous materials with complex structures.
In addition, various preparation methods are proposed in order to obtain porous metal materials with different properties, but the conventional preparation techniques of the porous metal materials are mainly classified into a solid metal sintering method (such as a powder metallurgy method for preparing the sintered porous metal materials), a liquid metal solidification method (such as a casting method and a melt foaming method for preparing the foamed metal), a metal deposition method (such as a sputtering method and a reactive deposition method for preparing the foamed metal), and a 3D printing method. Wherein, other than 3D printing techniques, complex structures cannot be prepared by other techniques. Although the 3D printing technology can customize a finished product with a complex structure, the current 3D printing method generally directly prepares the porous metal material by controlling the laser power and the powder laying parameters, and since the 3D printing has limited accuracy, the size of the obtained pores is large, and the pores are often as high as hundreds of micrometers. The direct use of 3D printing techniques is limited by the precision problem that it is difficult to directly form secondary porous structures, and the direct use of dealloying can result in uniform porous structures with micropores, but cannot achieve hierarchical porous structures, and requires a long time, and cannot flexibly design the configuration of porous structures.
Disclosure of Invention
Aiming at the defects of the prior art, the invention aims to provide a preparation method of a porous metal material with a secondary porous structure, which mainly comprises the following key steps: raw material preparation → three-dimensional CAD model establishment → selected area laser melting forming → dealloying.
In order to achieve the purpose, the invention adopts the following technical scheme:
the invention relates to a preparation method of a porous metal material with a secondary porous structure, which comprises the following steps: mixing the metal A and the metal B to obtain mixed powder, forming the mixed powder through laser region selection to obtain a blank body with a primary porous structure, placing the blank body in an electrolyte, and performing dealloying reaction to obtain a porous metal material with a secondary porous structure;
the electrode potential of the component with the lowest electrode potential in the metal A is larger than that of the component with the highest electrode potential in the metal B.
The preparation method comprises the steps of firstly preparing a primary porous structure with a specific morphology by utilizing a selective laser melting technology, then corroding relatively active metal in a forming structure by utilizing dealloying, and forming a nano porous structure with a three-dimensional communication network by using the residual inert elements in a surface diffusion or aggregation mode to finally obtain the porous metal material with a secondary porous structure.
Preferably, the metal a is at least one selected from tantalum, gold, silver, tin, niobium, titanium, copper, iron, aluminum, nickel, chromium, cobalt, zinc, lead and platinum, and preferably one selected from tantalum, niobium, gold and copper.
Preferably, the metal B is at least one selected from the group consisting of silver, tin, tantalum, niobium, titanium, copper, iron, aluminum, nickel, chromium, cobalt, zinc, lead, and magnesium, and preferably one selected from the group consisting of titanium, copper, silver, niobium, and nickel.
The inventors have found that when the above-mentioned single metal is selected for both metal a and metal B, the properties of the finally obtained porous metal material are optimal.
In a preferred embodiment, the particle size of the metal A is < 53 μm, preferably 15 to 53 μm.
In a preferred embodiment, the particle size of the metal B is < 53 μm, preferably 15 to 53 μm.
The particle size of the metal A and the particle size of the metal B are controlled within the range, so that the obtained mixed powder has excellent fluidity, the compactness in the subsequent printing process is optimal, if the particle size is too small, the powder has poor fluidity, and if the particle size is too large, the phenomenon of uneven powder spreading in the 3D printing forming process can be caused, so that the formed part has the defects of large pores, interlayer cracks and the like.
In a preferable scheme, the mixing mode is ball milling, the rotating speed of the ball milling is 40-100r/min, and the ball-to-material ratio is 1.5-2.2: 1.
Controlling the ball milling parameters in the above range can make the mixing of the metal A and the metal B most uniform, and finally make the secondary porous distribution of the metal material obtained after the alloy removal uniform.
In the actual operation process, when the ball milling is carried out, the GMS ball mill with the model of GMS20-2 is used, in order to avoid the problem that the oxygen content in the powder is increased due to the mixing of oxygen in the powder mixing process to influence the performance of the powder, argon is introduced into a ball milling tank to completely discharge air, and the ball milling tank is sealed and placed on the ball mill. After the powder mixing is finished, the powder is taken out of the ball milling tank as soon as possible to avoid the oxidation of the powder, and is stored in a sealing way or is placed in printing equipment.
Preferably, the mass fraction of the metal A in the mixed powder is 10-90%, preferably 30-50%.
In a preferred scheme, the process parameters of the selective laser area forming are as follows: the laser power is 150W-400W, preferably 250-350W, the scanning speed is 200-1000 mm/s, preferably 300-500 mm/s, the scanning distance is 80-150 mu m, preferably 90-120 mu m, the thickness of a single-layer powder spreading layer is 20-100 mu m, preferably 30-50 mu m, the preheating temperature of the substrate is 100-180 ℃, and preferably 100-150 ℃.
In a preferable scheme, the aperture of the green body with the primary porous structure is 200-800 μm, and is preferably 400-600 μm.
In the invention, powder suitable for 3D printing forming is obtained by coordinating the particle size of raw materials and a ball milling process, then a forming process of a 3D printing technology is regulated to prepare a porous blank with the aperture of 200-800 mu m, and finally secondary porosity is regulated by dealloying solution ratio and electrochemical corrosion time to finally obtain secondary porosity.
The inventor finds that the pore diameter of the primary porous is controlled within the range, the finally formed secondary porous structure is best, and the performance of the finally obtained porous metal material is optimal.
In the actual operation process, three-dimensional modeling is firstly carried out, a part model required to be prepared is established by using Magics three-dimensional modeling software, the model is led into a main machine of selective laser melting equipment in an STL file format, then the selective laser melting equipment is debugged, a substrate is preheated and adjusted to be horizontal, then the substrate is uniformly mixed and paved into a powder supply cylinder of the selective laser melting equipment, powder is paved manually, a layer of uniform and thick mixed powder is paved on a substrate of a forming cylinder, a cabin door is closed, in order to prevent the composite powder from being oxidized in the printing process, argon is flushed into a forming cavity, the oxygen content in the cavity is enabled to be lower than 0.1%, gas circulation is started, then appropriate printing parameters are set in the three-dimensional model, and laser selective forming is carried out.
Preferably, the electrolyte is selected from acid solution, and the acid in the acid solution is selected from HF and HNO3、H2SO4And HCl.
More preferably, the volume fraction of the acid in the acid solution is 0.5% to 2%.
In the preferred scheme, the dealloying temperature is 20-30 ℃, and the dealloying time is 8-24 hours.
In the method, a certain proportion of acid solution is used as electrolyte, a blank obtained by 3D printing is placed in the electrolyte to be subjected to constant-temperature water bath dealloying, in the dealloying process, the metal A phase and the metal B phase form a large number of primary battery systems together with the electrolyte, in the primary battery system, the metal B phase is an anode and is corroded and dissolved with the electrolyte, the metal A phase is used as a cathode to be protected and is not dissolved, and therefore the porous metal material with the secondary porous structure is obtained.
Advantageous effects
The preparation method comprises the steps of firstly preparing a primary porous structure with a specific morphology by utilizing a selective laser melting technology, then corroding relatively active metal in a forming structure by utilizing dealloying, and forming a nano porous structure with a three-dimensional communication network by using the residual inert elements in a surface diffusion or aggregation mode to finally obtain the porous metal material with a secondary porous structure.
The preparation method provided by the invention has the advantages of simple process and controllable pore structure, and is suitable for industrial production.
Drawings
FIG. 1 is a macro-topographic map of porous tantalum with a secondary porous structure prepared in example 1.
FIG. 2 is a micro-topography of porous tantalum with secondary porosity prepared in example 1.
FIG. 3 is a micro-topography of porous tantalum with secondary porosity as prepared in example 2.
FIG. 4 is a micro-topography of porous tantalum with secondary porosity as prepared in example 3.
Detailed Description
Example 1
Spherical tantalum powder and titanium powder with the particle size of 15-53 mu m are used, and the ratio of the spherical tantalum powder to the titanium powder is (2): 1, ball milling for 12 hours by using a GMS20-2 ball mill to obtain tantalum-titanium composite powder, wherein tantalum is an A component, the mass fraction is 60%, titanium is a B component, the powder is laid in a powder supply cylinder of selective laser melting equipment, a substrate is preheated to 100 ℃, the substrate is leveled and laid with powder, a cabin door is closed, argon is filled for protection, oxidation is prevented, a three-dimensional model is established through Magics, the model structure is a diamond structure, and the oxygen content in the forming cabin is lower than 0.1% starts laser printing and forming, the layer thickness is 0.03mm, the scanning distance is 0.09mm, the spot diameter is 110 mu m, the power is 250W, the scanning speed is 300mm/s, the rotation angle between scanning layers is 67 degrees, after printing is finished, a primary porous blank body with the pore diameter of 400-600 mu m is obtained, a porous sample is cut off by linear cutting, the blank body is cleaned by alcohol by ultrasonic equipment and then dried, dealloying is carried out, HNO with the volume fraction of 1% is used3And (3) using the mixed solution of + 1% HF as a corrosive agent, placing the printed parts in the corrosive agent, carrying out constant-temperature water bath at 25 ℃ for 12h, taking out the parts, respectively cleaning with acetone and alcohol, and drying. The porous tantalum with the secondary porous structure is obtained, the actual porosity of the sample is 70.5%, the elastic modulus is 1.9GPa, and the compressive strength is 71 MPa. The macro topography and the surface micro topography of the sample after the alloy is removed are shown in figure 1, and the pore size of the surface of the sample is about 2 mu m.
Example 2
Spherical tantalum powder and titanium powder with the particle size of 15-53 mu m are used, and the ratio of the spherical tantalum powder to the titanium powder is (2): 1, ball milling for 12 hours by using a GMS20-2 ball mill to obtain tantalum-nickel composite powder, wherein the tantalum is the component A, the mass fraction is 35 percent, the nickel is the component B, the powder is spread in a powder supply cylinder of selective laser melting equipment, a substrate is preheated to 100 ℃, and after leveling and powder spreading, closing the cabin door, introducing argon for protection, preventing oxidation, establishing a three-dimensional model through Magics, wherein the model structure is a diamond structure, starting laser printing and forming when the oxygen content in the forming cabin is lower than 0.1 percent, wherein the layer thickness is 0.03mm, the scanning interval is 0.09mm, the spot diameter is 110 mu m, the power is 250W, the scanning speed is 300mm/s, the rotation angle between scanning layers is 67 degrees, and obtaining a primary porous blank with the aperture of 400-600 microns, cutting a porous sample by linear cutting, cleaning the sample by alcohol by using ultrasonic equipment, drying, dealloying and using HNO with the volume fraction of 1%.3And (3) taking the HF mixed solution with the concentration of 1% as a corrosive agent, putting the printed parts into the corrosive agent, carrying out constant-temperature water bath at 25 ℃ for 24 hours, taking out the parts, respectively cleaning with acetone and alcohol, and drying. The actual porosity of the sample is 69.5%, the elastic modulus is 1.9GPa, and the compressive strength is 70 MPa. The microstructure is shown in figure 2, and a three-dimensional connected pore structure is formed, the pore diameter is about 2 mu m, and the strength of the sample is not reduced.
Example 3
Spherical tantalum powder and titanium powder with the particle size of 15-53 mu m are used, and the ratio of the spherical tantalum powder to the titanium powder is (2): 1, ball milling for 12 hours by using a GMS20-2 ball mill to obtain tantalum-chromium composite powder, wherein tantalum is an A component and has a mass fraction of 35 percent, chromium is a B component, the powder is laid in a powder supply cylinder of selective laser melting equipment, a substrate is preheated to 100 ℃, after leveling and powder laying, a cabin door is closed, argon is filled for protection to prevent oxidation, a three-dimensional model is established by Magics, the model structure is a diamond structure, laser printing forming is started when the oxygen content of the forming cabin is lower than 0.1 percent, the layer thickness is 0.03mm, the scanning interval is 0.09mm, the spot diameter is 110 mu m, the power is 250W, the scanning speed is 300mm/s, the scanning interlayer rotation angle is 67 degrees, after printing, a primary porous blank with the pore diameter of 500 plus 700 mu m is obtained, cutting is performed by linear cutting, an ultrasonic equipment is used for cleaning by alcohol and drying, dealloying is performed, HF mixed solution with the volume fraction of 0.5 percent is used as a corrosive agent, and (3) placing the printed part in a corrosive agent, carrying out constant-temperature water bath at 25 ℃ for 12h, taking out the part, respectively cleaning with acetone and alcohol, and drying. The actual porosity of the sample is 70.2%, the elastic modulus is 1.8GPa, and the compressive strength is 76 MPa. The micro-topography is shown in FIG. 3.
Example 4
Spherical copper powder and aluminum powder with the particle size of 15-53 mu m are used, and the ratio of the spherical copper powder to the spherical aluminum powder is 2:1, ball milling for 12 hours by using a GMS20-2 ball mill to obtain copper-aluminum composite powder, wherein copper is a component A, the mass fraction is 25%, aluminum is a component B, the powder is laid in a powder supply cylinder of selective laser melting equipment, a substrate is preheated to 100 ℃, and after leveling and powder laying, closing the cabin door, introducing argon for protection, preventing oxidation, establishing a three-dimensional model through Magics, wherein the model structure is a diamond structure, starting laser printing and forming when the oxygen content in the forming cabin is lower than 0.1 percent, wherein the layer thickness is 0.03mm, the scanning interval is 0.09mm, the spot diameter is 110 mu m, the power is 250W, the scanning speed is 600mm/s, the rotation angle between scanning layers is 67 degrees, obtaining a primary porous blank with the aperture of 600-.O3And (3) taking the solution as a corrosive agent, placing the printed part in the corrosive agent, carrying out constant-temperature water bath at 25 ℃ for 8h, taking out the part, respectively cleaning with acetone and alcohol, and drying. The actual porosity of the sample is 76.2%, the elastic modulus is 0.8GPa, and the compressive strength is 36 MPa.
Example 5
Spherical niobium powder and copper powder with the particle size of 15-53 mu m are used, and the ratio of the spherical powder to the copper powder is (2): 1, ball milling for 12 hours by using a GMS20-2 ball mill to obtain niobium-copper composite powder, wherein niobium is a component A with the mass fraction of 25 percent, copper is a component B, the powder is spread in a powder supply cylinder of selective laser melting equipment, a substrate is preheated to 100 ℃, and after leveling and powder spreading, closing the cabin door, introducing argon for protection, preventing oxidation, establishing a three-dimensional model through Magics, wherein the model structure is a diamond structure, starting laser printing and forming when the oxygen content in the forming cabin is lower than 0.1 percent, wherein the layer thickness is 0.03mm, the scanning interval is 0.08mm, the spot diameter is 110 mu m, the power is 300W, the scanning speed is 800mm/s, the rotation angle between scanning layers is 67 degrees, obtaining a primary porous blank with the aperture of 400-600 mu m, cutting off a porous sample by linear cutting, cleaning the sample by alcohol by using ultrasonic equipment, drying the sample, performing dealloying, and using HNO with the volume fraction of 0.5%.3And (3) taking the solution as a corrosive agent, placing the printed part in the corrosive agent, carrying out constant-temperature water bath at 25 ℃ for 12h, taking out the part, respectively cleaning with acetone and alcohol, and drying. The actual porosity of the sample is 67.4%, the elastic modulus is 2.1GPa, and the compressive strength is 56 MPa.
Comparative example 1
The other conditions were the same as in example 1 except that the etchant was changed to 2% HNO3+ 1% HF mixed solution, water bath at 25 deg.c for 12 hr, actual porosity of the sample 79.1%, elastic modulus of 1.1GPa and compression strength of 26 MPa.
Comparative example 2
The other conditions were the same as in example 1 except that the constant-temperature water bath time at 25 ℃ was changed to 6 hours, the actual porosity of the sample was 62.3%, the elastic modulus was 2.4GPa, and the compressive strength was 95 MPa. The secondary pores can not be communicated with each other, and the proportion of the pores is low.
Comparative example 3
The other conditions were the same as in example 1 except that the etchant was changed to 2% HNO3+ 0.5% HF mixed solution, constant temperature water bath for 12h, actual porosity of the sample being 73.3%, elastic modulus being 1.6GPa, compressive strength being 54 MPa.
Claims (10)
1. A preparation method of a porous metal material with a secondary porous structure is characterized by comprising the following steps: the method comprises the following steps: mixing the metal A and the metal B to obtain mixed powder, forming the mixed powder through laser region selection to obtain a blank body with a primary porous structure, placing the blank body in an electrolyte, and performing dealloying reaction to obtain a porous metal material with a secondary porous structure;
the electrode potential of the component with the lowest electrode potential in the metal A is larger than that of the component with the highest electrode potential in the metal B.
2. The method for preparing a porous metal material having a secondary porous structure according to claim 1, wherein: the metal A is at least one of tantalum, gold, silver, tin, niobium, titanium, copper, iron, aluminum, nickel, chromium, cobalt, zinc, lead and platinum,
the metal B is at least one selected from silver, tin, tantalum, niobium, titanium, copper, iron, aluminum, nickel, chromium, cobalt, zinc, lead and magnesium.
3. The method for preparing a porous metal material having a secondary porous structure according to claim 2, wherein:
the metal A is selected from one of tantalum, niobium, gold and copper;
the metal B is selected from one of titanium, copper, silver, niobium and nickel.
4. The method for preparing a porous metal material having a secondary porous structure according to claim 1, wherein: the grain diameter of the metal A is less than 53 mu m, and the grain diameter of the metal B is less than 53 mu m.
5. The method for preparing a porous metal material having a secondary porous structure according to claim 1, wherein: the mixing mode is ball milling, the rotating speed of the ball milling is 40-100r/min, and the ball-to-material ratio is 1.5-2.2: 1.
6. The method for preparing a porous metal material having a secondary porous structure according to claim 1, wherein: in the mixed powder, the mass fraction of the metal A is 10-90%.
7. The method for preparing a porous metal material having a secondary porous structure according to claim 1, wherein: the technological parameters of the selective laser forming are as follows: the laser power is 150W-400W, the scanning speed is 200-1000 mm/s, the scanning interval is 80-150 mu m, the thickness of a single-layer powder spreading layer is 20-100 mu m, and the preheating temperature of the substrate is 100-180 ℃.
8. The method for preparing a porous metal material with a secondary porous structure as claimed in claim 1, wherein: the aperture of the primary porous structure blank is 200-800 mu m.
9. The method for preparing a porous metal material having a secondary porous structure according to claim 1, wherein: the electrolyte is selected from acid solution, and the acid in the acid solution is selected from HF and HNO3、H2SO4At least one of HCl;
in the acid solution, the volume fraction of the acid is 0.5-2%.
10. The method for preparing a porous metal material having a secondary porous structure according to claim 1, wherein: the dealloying temperature is 20-30 ℃, and the dealloying time is 8-24 hours.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210224259.9A CN114589314A (en) | 2022-03-07 | 2022-03-07 | Preparation method of porous metal material with secondary porous structure |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210224259.9A CN114589314A (en) | 2022-03-07 | 2022-03-07 | Preparation method of porous metal material with secondary porous structure |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN114589314A true CN114589314A (en) | 2022-06-07 |
Family
ID=81808118
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210224259.9A Pending CN114589314A (en) | 2022-03-07 | 2022-03-07 | Preparation method of porous metal material with secondary porous structure |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN114589314A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115533122A (en) * | 2022-12-01 | 2022-12-30 | 四川工程职业技术学院 | Iron-based alloy body and forming method and application thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108213408A (en) * | 2018-01-11 | 2018-06-29 | 中南大学 | A kind of method that the porous metal parts with labyrinth are prepared using 3D printing technique |
| CN109402439A (en) * | 2018-12-17 | 2019-03-01 | 广东省新材料研究所 | Across scale hierarchical porous structure porous nickel and the preparation method and application thereof |
| CN112048635A (en) * | 2020-08-25 | 2020-12-08 | 西安理工大学 | Micro-nano graded porous copper and preparation method thereof |
| CN113529158A (en) * | 2021-07-28 | 2021-10-22 | 西北有色金属研究院 | Process for preparing porous structure on surface of TC4 titanium alloy by electrochemical dealloying method |
| CN114134362A (en) * | 2021-11-18 | 2022-03-04 | 昆明理工大学 | Preparation method of large-size high-strength three-stage composite porous magnesium-silver alloy |
-
2022
- 2022-03-07 CN CN202210224259.9A patent/CN114589314A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108213408A (en) * | 2018-01-11 | 2018-06-29 | 中南大学 | A kind of method that the porous metal parts with labyrinth are prepared using 3D printing technique |
| CN109402439A (en) * | 2018-12-17 | 2019-03-01 | 广东省新材料研究所 | Across scale hierarchical porous structure porous nickel and the preparation method and application thereof |
| CN112048635A (en) * | 2020-08-25 | 2020-12-08 | 西安理工大学 | Micro-nano graded porous copper and preparation method thereof |
| CN113529158A (en) * | 2021-07-28 | 2021-10-22 | 西北有色金属研究院 | Process for preparing porous structure on surface of TC4 titanium alloy by electrochemical dealloying method |
| CN114134362A (en) * | 2021-11-18 | 2022-03-04 | 昆明理工大学 | Preparation method of large-size high-strength three-stage composite porous magnesium-silver alloy |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115533122A (en) * | 2022-12-01 | 2022-12-30 | 四川工程职业技术学院 | Iron-based alloy body and forming method and application thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US8268383B2 (en) | Medical implant and production thereof | |
| Singh et al. | Titanium foams for biomedical applications: a review | |
| CN108213408B (en) | Method for preparing porous metal part with complex structure by using 3D printing technology | |
| CN110508788B (en) | Preparation method of zinc or zinc alloy or composite material tissue engineering scaffold thereof | |
| US20060285991A1 (en) | Metal injection moulding for the production of medical implants | |
| CN102548589A (en) | Biodegradable implant and method for manufacturing same | |
| CN106421904A (en) | Method for preparing porous implant through gelcasting 3D printing and electroreduction | |
| JP2003524072A (en) | Method for producing metal foam by electrolytic reduction of porous oxide preform | |
| CN104674320A (en) | Preparation method and application of wear-resistant antibacterial bioactive ceramic film for titanium or titanium alloy surface | |
| CN103421997A (en) | Degradable Mg-Zn-Si-Ca magnesium-based biological ceramic composite implant material and preparation method thereof | |
| AU2008272658B2 (en) | A process for realising biologically- compatible three- dimensional elements | |
| CN109128186A (en) | A kind of scope mucous membrane decollement electric knife head and preparation method thereof | |
| CN106676605B (en) | Preparation method and applications with the porous pure titanium of lattice structure or titanium alloy surface multiporous biological active ceramic film | |
| CN111631842B (en) | Method for preparing bone defect prosthesis | |
| CN114589314A (en) | Preparation method of porous metal material with secondary porous structure | |
| JP5846591B2 (en) | Implant | |
| CN110157936B (en) | Preparation method of biomedical ordered porous as-cast zinc-based material | |
| CN111467577B (en) | Medical metal bone implant material | |
| CN111363995B (en) | Preparation method of medical metal bone implant material | |
| Xue et al. | Strengthening Mechanisms of Ti–Mg Composite for Biomaterials: A Review | |
| CN113026013A (en) | Preparation method of corrosion-resistant zirconium-based amorphous alloy composite material coating | |
| CN109280828A (en) | A kind of high-strength degradable implantation instrument composite material and preparation method | |
| CN114749659B (en) | Method for preparing secondary porous tantalum metal part by 3D printing | |
| İzmir et al. | Ti6Al4V foams having nanotubular surfaces for orthopaedic applications | |
| CN102580150A (en) | Gradient bioactive ceramic coating material containing samarium oxide and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20220607 |
|
| RJ01 | Rejection of invention patent application after publication |