US20200198008A1 - Method for the powder-metallurgical production of components from titanium or titanium alloys - Google Patents

Method for the powder-metallurgical production of components from titanium or titanium alloys Download PDF

Info

Publication number
US20200198008A1
US20200198008A1 US16/093,197 US201716093197A US2020198008A1 US 20200198008 A1 US20200198008 A1 US 20200198008A1 US 201716093197 A US201716093197 A US 201716093197A US 2020198008 A1 US2020198008 A1 US 2020198008A1
Authority
US
United States
Prior art keywords
sintering
titanium
grain size
titanium alloy
sintering step
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.)
Abandoned
Application number
US16/093,197
Other languages
English (en)
Inventor
Ulf VIEHÖFER
Wendelin Winkelmüller
Markus Lang
Matthias SCHARVOGEL
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Element 22 GmbH
Original Assignee
Element 22 GmbH
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Element 22 GmbH filed Critical Element 22 GmbH
Assigned to Element 22 GmbH reassignment Element 22 GmbH ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: LANG, MARKUS, SCHARVOGEL, Matthias, WINKELMULLER, WENDELIN
Assigned to Element 22 GmbH reassignment Element 22 GmbH ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: VIEHÖFER, Ulf
Publication of US20200198008A1 publication Critical patent/US20200198008A1/en
Abandoned legal-status Critical Current

Links

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
    • 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
    • B22F3/1003—Use of special medium during sintering, e.g. sintering aid
    • B22F3/1007—Atmosphere
    • B22F1/0011—
    • 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
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/05—Metallic powder characterised by the size or surface area of the particles
    • 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
    • B22F3/12—Both compacting and sintering
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/045—Alloys based on refractory metals
    • C22C1/0458—Alloys based on titanium, zirconium or hafnium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
    • 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
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/20—Refractory metals
    • B22F2301/205—Titanium, zirconium or hafnium
    • 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
    • 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
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
    • 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

Definitions

  • the present invention relates to a method for the powder-metallurgical production of a component from titanium or a titanium alloy, wherein first, using metal powder produced from titanium or the titanium alloy, a green part is formed and this is densified and compacted in a subsequent sintering step.
  • the objective of forming is to bring the titanium powder particles into the tightest possible packing in a form close to the final contour.
  • additives are used which must be removed in one or more subsequent debinding step(s).
  • the subsequent process step frequently also the final one, sintering, the powder particles are consolidated by material transport.
  • Titanium has two crystal modifications.
  • the hexagonal a phase which with pure titanium and normal pressure is present up to a temperature of 882.5° C.
  • the cubic space-centered ⁇ phase which with pure titanium and normal pressure occurs above the aforementioned temperature.
  • the presence of the different phases at room temperature is used to classify titanium alloys into ⁇ -Ti, ( ⁇ + ⁇ )-Ti and ⁇ -Ti alloys.
  • Ti6Al4V for example, is an ( ⁇ + ⁇ )-alloy, i.e., both phases are present in the grain structure at room temperature.
  • sintering temperatures of about 1100-1400° C. at a sintering duration of about 2-5 h are needed.
  • pure titanium and Ti6Al4V this means that the materials are processed in the p-phase region, which leads to a massive p-grain growth.
  • the grain structure of a Ti6Al4V sample produced in the standard manner from titanium powders commonly used in the prior art (with powder grain sizes ⁇ 45 ⁇ m) and sintered under sintering conditions typically used in the prior art is shown in FIG. 2 .
  • One goal generally pursued with the invention is that of creating the possibility, is in the case of powder-metallurgically produced and sintered titanium components, of manipulating the grain structure and optimizing the material properties.
  • the intention was to make it possible to adapt the material properties to the specific use case directly in the sintering process and/or to create, during the sintering process, an optimal starting point for further thermal treatment steps after sintering.
  • a process comprises a method for the powder-metallurgical production of a component from titanium or a titanium alloy, wherein first, using metal powder from titanium or the titanium alloy, a green part is formed and this is densified and compacted in a subsequent sintering step, characterized in that for producing the green part, metal powder from titanium or titanium alloy with a mean grain size of ⁇ 25 ⁇ m, measured using laser diffraction according to ASTM B822-10 is used and that the sintering step is performed at a sintering temperature up to a maximum of 1100° C., at a sintering duration of ⁇ 5 h in an atmosphere under a reduced pressure in comparison with normal pressure.
  • the maximum grain size of the metal powder from titanium or the titanium alloy is ⁇ 30 ⁇ m; that the sintering step is performed under a vacuum with a pressure of 10 ⁇ 3 mbar, especially at a pressure of 10 ⁇ 5 mbar; and that the sintering step is performed in an inert gas atmosphere, especially an argon atmosphere, at a pressure of ⁇ 300 mbar.
  • the sintering duration is 3.5 h, in particular of s 3 h, preferably of ⁇ 2.5 h.
  • the sintering duration is at least 1 h, preferably at least ⁇ 2 h.
  • the sintering temperature is up to a maximum of 1050° C., preferably up to a maximum of temperature up to a maximum of 1000° C., especially up to a maximum of 950° C. and the sintering temperature amounts to at least 860° C.
  • the method is further characterized in that in the sintering step, the sintering temperature is adjusted in the range below a ⁇ -transition temperature of the titanium or titanium alloy material.
  • the component after the sintering step has a material density of >97%, in particular >98%, preferably 99%.
  • a material density in the component of >97% is selected and that to achieve a material density in the component of >97%, after the sintering step this is exposed to an additional step with pressure and optionally a temperature, e.g., a step of cold isostatic pressing (CIP) and/or hot isostatic pressing (HIP).
  • CIP cold isostatic pressing
  • HIP hot isostatic pressing
  • HIP hot isostatic pressing
  • URQ uniform rapid quench
  • An additional aspect to solving this problem lies in a titanium component that exhibits the properties that it has a globular ⁇ -structure with a grain size of ⁇ 30 ⁇ m; that it has a grain structure with globular ⁇ -structure with mean grain size of ⁇ 30 ⁇ m and lamellar ( ⁇ + ⁇ ) grain structure with a mean primary ⁇ -phase grain size of ⁇ 90 ⁇ m; and/or that it has a lamellar ( ⁇ + ⁇ ) grain structure with a mean primary to ⁇ -phase grain size of ⁇ 120 ⁇ m.
  • FIG. 1 a representation of a lamellar ( ⁇ + ⁇ ) grain structure of a Ti6Al4V sample with description of the gran structure fractions according to Sieniawski et al. [3];
  • FIG. 2 an enlarged photomicrograph of a standard sintered Ti6Al4V sample, produced by powder-metallurgically using powder particles ⁇ 45 ⁇ m and standard-sintered and confirms a lamellar ( ⁇ + ⁇ ) grain structure for this;
  • FIG. 3 a schematic representation of the effect of reducing the grain size by half (using the example of spherical particles) on the number of particles required to fill a defined volume;
  • FIG. 4 a schematic representation of the reduction in size of the hollow space between adjacent particles due to reducing the grain size by half (using the example of spherical particles);
  • FIG. 5 an enlarged polished micrograph section of a powder-metallurgically produced and sintered Ti6Al4V sample made from powder particles ⁇ 20 ⁇ m, confirming the formation of a distinct globular ⁇ -structure;
  • FIG. 6 an enlarged polished micrograph section of a powder-metallurgically produced and sintered Ti6Al4V sample made from powder particles ⁇ 20 ⁇ m, confirming the formation of a bimodal grain structure with a globular ⁇ -structure and distinct lamellar ( ⁇ + ⁇ ) grain structure.
  • An essential prerequisite for implementing the process according to the invention and creating the possibility of influencing the material properties in the sintering process is the use of metal powder, produced from titanium or a titanium alloy, with a mean grain size of ⁇ 25 ⁇ m, so-called fine powder.
  • the maximum grain size may in particular be ⁇ 30 ⁇ m.
  • the maximum grain size is specified as a limit value by the manufacturers of such fine powders.
  • a small fraction of particles in such batches can always have grain sizes above this limit.
  • Such a fraction, as a rule is generally specified as a maximum of 1 to a maximum of 5 wt.-%.
  • the mean grain size may advantageously even be lower, especially ⁇ 20 ⁇ m, advantageously ⁇ 10 ⁇ m and particularly preferably even ⁇ 5 ⁇ m.
  • the measurement of the grain sizes essential for the invention and the distribution thereof is performed by grain size testing using laser diffraction according to ASTM B822-10 (published 2010), valid at the time of this application.
  • the grain size distribution is determined by wt.-% and according to D10/D50/D90, wherein D50 is the mean grain size.
  • the grain sizes given here in comparison tests were measured using the COULTER® LS grain size analyzer made by Beckman Coulter and evaluated using the Fraunhofer theory according to ASTM B822-10.
  • the grain size in the sense of the invention is specified as the particle diameter.
  • the grain size corresponds to the projected maximum particle dimension.
  • the surface area in the nonconsolidated component available for the sintering process increases, and thus so does the stored surface energy. Since the reduction of this energy is the driving force in the sintering process, the sintering process can then take place using little thermal energy.
  • An additional advantage of using fine powders of the sizes indicated above for forming the green part is that more powder particles can be introduced per unit volume. In addition to the enlarged surface, this leads to a higher number of contact points per unit volume, as shown in FIG. 3 .
  • FIG. 3 There, in a schematic representation, the effect of reducing the grain size by half (using the example of spherical particles) on the particle count to fill a defined volume is shown.
  • the contact points of the particles in turn are the starting point and a necessary condition for the sintering process, which is driven by diffusion processes.
  • the increased number of such contact points per unit volume therefore improves the starting conditions for the sintering process.
  • FIG. 4 in a schematic representation the decrease in size of the hollow space between adjacent particles is illustrated by reducing the grain size by half (using the example of spherical particles). Since this hollow space must be closed to achieve the—high—material density desired for the component following the sintering process must be closed by material transport during the sintering process, a smaller volume to be covered is an additional decisive reason for an improvement in the process result.
  • the sintering step typically takes place in a reduced-pressure atmosphere.
  • This can be a vacuum with a pressure of ⁇ 10 ⁇ 3 mbar, especially 10 ⁇ 5 mbar.
  • it may also be a reduced-pressure inert gas atmosphere with a pressure of, e.g., 300 mbar.
  • Argon gas in particular is considered as the inert gas here.
  • the sintering temperatures according to the invention are below 1100° C. They can in particular be a maximum of 1050° C., a maximum of 1000° C., and even a maximum of only 950° C. Preferably, however, to achieve a good sintering result, the sintering temperature selected advantageously should not be below 860° C.
  • the sintering temperature may be kept uniform. In particular, however, it is also possible and falls within the meaning of the invention to vary the temperature during the sintering process.
  • the sintering temperature is defined here as the temperature that the workpiece to be sintered has undergone.
  • an adapted process temperature is to be selected, which distinguishes the process temperature measured at a distance remote from the workpiece from the sintering temperature undergone by the workpiece.
  • the duration of sintering may especially be ⁇ 3.5 h, often also ⁇ 3 h or even ⁇ 2.5 h. However, it was found that as a rule, for achieving good results, the sintering time should amount to at least 1 hour, preferably at least 2 hours.
  • components from titanium or titanium alloys produced with the method of the invention generally have a final density of >97%. However, final densities above 98% may also be reached, even ⁇ 99%.
  • the titanium components are sintered at less than the ⁇ -transition temperature (e.g., at a temperature 30° C. below the ⁇ -transition temperature.
  • the ⁇ -transition temperature of Ti6Al4V falls in the range of 985° C. to 1015° C. [3; 5]. This relatively wide range given in the literature is attributable, on one hand, to the distribution of the alloying elements in the titanium alloys. On the other hand, the ambient pressure is an additional influential factor. For example, Huang et al. describe that as a result of elevated process pressures (1500 bar), a reduction of the ⁇ -transition temperature can be observed in the alloy Ti4Al8Nb [6].
  • the components were sintered close to the ⁇ -transition temperature, but still below this.
  • the lamellar grain structure with reduced primary ⁇ -phase grain size of the Ti6Al4V alloy which is also advantageous for many use cases
  • initially samples were produced in which the titanium components were sintered at a sintering temperature of 1000° C. ( FIG. 6 ).
  • this sintering temperature was still below the ⁇ -transition temperature, although only slightly.
  • the bimodal grain structure formed is composed of globular ⁇ -structure and small portions of lamellar ( ⁇ + ⁇ ) structures, wherein the mean ⁇ -grain size is 81 ⁇ m.
  • the density measurement was performed according to the specifications of ASTM B962 and ASTM B311.
  • the grain size determination was performed according to the provisions of ASTM E112.
  • the components were largely sintered, i.e., for the greatest part of the time, below the ⁇ -transition temperature, but with a minimal hold time that remained below 30 min, preferably below 20 min, especially below 10 min, and also above the ⁇ -transition temperature in phases, so that the p-phase is entirely present, in order thus to create the lamellar grain structure, but also the primary ⁇ -phase grain does not exceed the size range of a globular ⁇ -structure with mean grain size of ⁇ 30 ⁇ m and lamellar ( ⁇ + ⁇ ) grain structure with a mean primary p-phase grain size of ⁇ 90 ⁇ m.
  • the sintering above the p-transition temperature always took place at a temperature in excess of 1015° C. This temperature was always kept below 1080° C., but advantageously was below 1040° C. and especially ⁇ 1020° C. was selected.
  • powder-metallurgical moldings from titanium and titanium alloys can be sintered at sintering temperatures below the usual mark of beyond 1100° C., generally 1200° C. or more, advantageously below the p-transition temperature, and thereby components with good structural and other material properties can be obtained. It was possible to show that at distinctly lower set sintering temperatures compared with the sintering temperatures customary in the prior art—unexpectedly—components with high final densities of >97% can be obtained.
  • the method according to the invention makes it possible to vary the grain structure of the titanium component in the sintering process and drastically reduce the grain size, which makes it possible to optimize the mechanical properties of the components, e.g., the tensile strength, ductility and fatigue strength.
  • a particularly low temperature may also be selected for sintering, e.g., a temperature below 950° C., can be selected, and if the desired material density in the finished component (generally >97%) is not yet achieved in such a sintering step, further compaction of the material can be performed in the subsequently performed pressing step, in which the material is subjected to pressure and optionally a temperature, especially by cold isostatic pressing (CIP) or hot isostatic pressing (HIP).
  • CIP cold isostatic pressing
  • HIP hot isostatic pressing
  • the material density after sintering may be at ⁇ 97%, and it may be compacted to >97% by the pressing step after sintering.
  • components produced according to the method of the invention may be subjected to additional thermal aftertreatments to further modify the properties of the materials.
  • additional thermal aftertreatments can, for example, be one or more of the following methods: hot isostatic pressing (HIP), quench, uniform rapid quench (URQ).
  • the lower sintering temperature compared to the sintering temperatures from the prior art also result in additional environmental/financial and process technology advantages. On one hand, less thermal energy is required in the sintering process, leading to lower costs but also to shorter processing times. On the other hand, the method in accordance with the invention performed with reduced sintering temperature also allows the use of how-wall furnace designs which are once again more economical than furnaces designed for process temperatures >1100° C., where cold-wall furnaces are typically used.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Powder Metallurgy (AREA)
US16/093,197 2016-04-14 2017-04-04 Method for the powder-metallurgical production of components from titanium or titanium alloys Abandoned US20200198008A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
EP16165222.7A EP3231536B8 (de) 2016-04-14 2016-04-14 Verfahren zur pulvermetallurgischen herstellung von bauteilen aus titan oder titanlegierungen
EP16165222.7 2016-04-14
PCT/EP2017/058015 WO2017178289A1 (de) 2016-04-14 2017-04-04 Verfahren zur pulvermetallurgischen herstellung von bauteilen aus titan oder titanlegierungen

Publications (1)

Publication Number Publication Date
US20200198008A1 true US20200198008A1 (en) 2020-06-25

Family

ID=55759489

Family Applications (1)

Application Number Title Priority Date Filing Date
US16/093,197 Abandoned US20200198008A1 (en) 2016-04-14 2017-04-04 Method for the powder-metallurgical production of components from titanium or titanium alloys

Country Status (22)

Country Link
US (1) US20200198008A1 (https=)
EP (1) EP3231536B8 (https=)
JP (1) JP2019516021A (https=)
KR (1) KR102341739B1 (https=)
CN (1) CN109311086B (https=)
AU (1) AU2017249647B2 (https=)
CA (1) CA3018808C (https=)
DK (1) DK3231536T3 (https=)
ES (1) ES2667872T3 (https=)
HU (1) HUE037106T2 (https=)
IL (1) IL262260B (https=)
MX (1) MX2018012547A (https=)
MY (1) MY183957A (https=)
NO (1) NO3231536T3 (https=)
NZ (1) NZ746808A (https=)
PL (1) PL3231536T3 (https=)
PT (1) PT3231536T (https=)
RU (1) RU2730353C2 (https=)
SA (1) SA518400144B1 (https=)
SG (1) SG11201808189VA (https=)
SI (1) SI3231536T1 (https=)
WO (1) WO2017178289A1 (https=)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP6750056B2 (ja) * 2019-02-27 2020-09-02 東邦チタニウム株式会社 チタン粉の製造方法、スポンジチタンの製造方法、チタン粉および、ガス収集装置
CN111299572B (zh) * 2019-11-28 2022-05-03 天钛隆（天津）金属材料有限公司 一种钛及钛合金无缝管的生产方法
PL450148A1 (pl) * 2024-10-28 2025-06-09 Politechnika Częstochowska Sposób wytwarzania warstwy bioaktywnej
CN120325976B (zh) * 2025-06-20 2025-10-28 西安欧中材料科技股份有限公司 采用SS-PREP和EIGA Ti6Al4V ELI球形粉末混合制备增材制造用基板的热等静压成形方法

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06306513A (ja) * 1993-04-22 1994-11-01 Nippon Steel Corp 高疲労強度焼結チタン合金の製造方法
US20120058002A1 (en) * 2007-06-11 2012-03-08 Advance Material Products, Inc.,(ADMA Products, Inc.) Manufacture of near-net shape titanium alloy articles from metal powders by sintering with presence of atomic hydrogen
US20150376397A1 (en) * 2011-11-30 2015-12-31 Seiko Epson Corporation Composition for injection molding, sintered compact, and method for producing sintered compact

Family Cites Families (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB818827A (en) * 1956-08-01 1959-08-26 Sintercast Corp America Improvements in or relating to methods for, and mould assemblies for, producing infiltrated articles
JPS5229407A (en) * 1975-09-02 1977-03-05 Miyamoto Kogyo Kk Process for production of titanium bars
FR2567153B1 (fr) 1984-07-06 1991-04-12 Onera (Off Nat Aerospatiale) Procede d'elaboration, par metallurgie des poudres, d'alliage a base de titane a faible dimension de grain
US5420400A (en) * 1991-10-15 1995-05-30 The Boeing Company Combined inductive heating cycle for sequential forming the brazing
JPH05345937A (ja) * 1992-04-17 1993-12-27 Nippon Steel Corp Ｔｉ−Ｆｅ−Ａｌ系焼結チタン合金の製造方法
JP3443175B2 (ja) * 1993-07-23 2003-09-02 アスラブ・エス アー 焼結によるチタン部品の製造方法およびこの種の製造方法を用いて作られる装飾品
US6551371B1 (en) * 1998-07-21 2003-04-22 Kabushiki Kaisha Toyota Chuo Kenkyusho Titanium-based composite material, method for producing the same and engine valve
WO2000006327A2 (de) 1998-07-29 2000-02-10 Fraunhofer-Gesellschaft zur Förderung der angewandten Forschung e.V. Verfahren zur herstellung von bauteilen durch metallpulverspritzguss
DE10332071B4 (de) 2003-07-10 2008-10-16 BLÜM, Heinz-Jürgen Verfahren und Vorrichtung zum kombinierten Entbindern und Sintern von Formteilen
CN1778980A (zh) * 2004-11-24 2006-05-31 台耀科技股份有限公司 金属粉末烧结体及其制造方法
RU2407817C2 (ru) * 2009-03-23 2010-12-27 Государственное образовательное учреждение высшего профессионального образования "Уральский государственный университет им. А.М. Горького" Способ получения пористого титана
KR20110061779A (ko) * 2009-12-02 2011-06-10 주식회사 티아이코리아 분말 사출 및 저온 소결에 의한 티타늄 성형체의 제조방법
AT509768B1 (de) * 2010-05-12 2012-04-15 Boehler Schmiedetechnik Gmbh & Co Kg Verfahren zur herstellung eines bauteiles und bauteile aus einer titan-aluminium-basislegierung
JP5760338B2 (ja) * 2010-06-25 2015-08-05 セイコーエプソン株式会社 粉末冶金用バインダー組成物、粉末冶金用コンパウンドおよび焼結体
WO2012148471A1 (en) * 2011-04-26 2012-11-01 The University Of Utah Powder metallurgy methods for the production of fine and ultrafine grain ti, and ti alloys
KR101367714B1 (ko) * 2012-03-29 2014-02-27 정성훈 티타늄 손톱깎이의 제조방법
CN103447533B (zh) * 2013-09-28 2015-04-01 重庆大学 一种制备开孔泡沫钛的方法

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06306513A (ja) * 1993-04-22 1994-11-01 Nippon Steel Corp 高疲労強度焼結チタン合金の製造方法
US20120058002A1 (en) * 2007-06-11 2012-03-08 Advance Material Products, Inc.,(ADMA Products, Inc.) Manufacture of near-net shape titanium alloy articles from metal powders by sintering with presence of atomic hydrogen
US20150376397A1 (en) * 2011-11-30 2015-12-31 Seiko Epson Corporation Composition for injection molding, sintered compact, and method for producing sintered compact

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
"Glossary of Metallurgical and Metalworking Terms," Metals Handbook, ASM Handbooks Online, ASM International, 2002, pp. 1, 116, 257. (Year: 2002) *

Also Published As

Publication number Publication date
CN109311086B (zh) 2021-08-13
JP2019516021A (ja) 2019-06-13
DK3231536T3 (en) 2018-05-14
KR102341739B1 (ko) 2021-12-20
PT3231536T (pt) 2018-05-08
MY183957A (en) 2021-03-17
WO2017178289A1 (de) 2017-10-19
CA3018808A1 (en) 2017-10-19
SG11201808189VA (en) 2018-10-30
EP3231536B1 (de) 2018-01-31
ES2667872T3 (es) 2018-05-14
EP3231536A1 (de) 2017-10-18
MX2018012547A (es) 2019-08-05
KR20180134953A (ko) 2018-12-19
NZ746808A (en) 2019-12-20
EP3231536B8 (de) 2018-08-08
SI3231536T1 (en) 2018-06-29
SA518400144B1 (ar) 2022-03-06
RU2018139866A3 (https=) 2020-05-14
AU2017249647A1 (en) 2018-10-25
PL3231536T3 (pl) 2018-11-30
IL262260B (en) 2019-08-29
RU2018139866A (ru) 2020-05-14
CA3018808C (en) 2021-08-31
NO3231536T3 (https=) 2018-06-30
IL262260A (en) 2018-11-29
AU2017249647B2 (en) 2019-09-05
HUE037106T2 (hu) 2018-08-28
CN109311086A (zh) 2019-02-05
RU2730353C2 (ru) 2020-08-21

Similar Documents

Publication Publication Date Title
CN104889379B (zh) 粉末冶金用金属粉末、复合物、造粒粉末及烧结体
AU2017249647B2 (en) Method for the powder-metallurgical production of components from titanium or titanium alloys
JP6314866B2 (ja) 粉末冶金用金属粉末、コンパウンド、造粒粉末および焼結体の製造方法
WO2012148471A1 (en) Powder metallurgy methods for the production of fine and ultrafine grain ti, and ti alloys
JP7758666B2 (ja) 三次元物体製造用の球状粉末
JP6308123B2 (ja) 粉末冶金用金属粉末、コンパウンド、造粒粉末および焼結体
US20030211001A1 (en) Manufacture of near-net shape titanium alloy articles from metal powders by sintering at variable pressure
Sygnatowicz et al. Processing of Dense ζ‐Ta 4 C 3− x by Reaction Sintering of Ta and TaC Powder Mixture
JP7684414B2 (ja) モリブデン粉末
Moon et al. A study on the microstructure of D023 Al3Zr and L12 (Al+ 12.5 at.% Cu) 3Zr intermetallic compounds synthesized by PBM and SPS
JP6299612B2 (ja) 粉末冶金用金属粉末、コンパウンド、造粒粉末および焼結体
JP2019516021A5 (https=)
JP6314842B2 (ja) 粉末冶金用金属粉末、コンパウンド、造粒粉末および焼結体
JP6311615B2 (ja) 粉末冶金用金属粉末、コンパウンド、造粒粉末および焼結体
JP2014055344A (ja) 焼結チタン合金およびその製造方法
TWI690600B (zh) 用於粉末冶金製造由鈦或鈦合金製成的構件的方法
JP6299610B2 (ja) 粉末冶金用金属粉末、コンパウンド、造粒粉末および焼結体
HK1262563B (zh) 用粉末冶金术制备钛或钛合金组件的方法
HK1262563A1 (en) Method for the powder-metallurgical production of components from titanium or titanium alloys
Kruzhanov et al. Suitability of Novel Titanium Powder for Metal Injection Moulding Application
WO2026019641A1 (en) Methods of obtaining full-density and fine grain sintered titanium components
Silva et al. Influence of heat treatment on the microstructure of a sintered bronze-aluminum alloy
WO2024163996A2 (en) Methods of making gold-titanium alloys from sintered powders
CN118900922A (zh) 合金粉末、基于所述合金制造部件的方法和所产生的部件
Nobrega et al. PM NonFerrous Materials: MIM Processing of Two Nickel-based Superalloys in a PADS Reactor

Legal Events

Date Code Title Description
AS Assignment

Owner name: ELEMENT 22 GMBH, GERMANY

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:WINKELMULLER, WENDELIN;LANG, MARKUS;SCHARVOGEL, MATTHIAS;REEL/FRAME:047145/0560

Effective date: 20180925

AS Assignment

Owner name: ELEMENT 22 GMBH, GERMANY

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:VIEHOEFER, ULF;REEL/FRAME:048508/0404

Effective date: 20190227

STPP Information on status: patent application and granting procedure in general

Free format text: NON FINAL ACTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: RESPONSE TO NON-FINAL OFFICE ACTION ENTERED AND FORWARDED TO EXAMINER

STPP Information on status: patent application and granting procedure in general

Free format text: FINAL REJECTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: RESPONSE AFTER FINAL ACTION FORWARDED TO EXAMINER

STPP Information on status: patent application and granting procedure in general

Free format text: DOCKETED NEW CASE - READY FOR EXAMINATION

STPP Information on status: patent application and granting procedure in general

Free format text: NON FINAL ACTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: RESPONSE TO NON-FINAL OFFICE ACTION ENTERED AND FORWARDED TO EXAMINER

STPP Information on status: patent application and granting procedure in general

Free format text: FINAL REJECTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: DOCKETED NEW CASE - READY FOR EXAMINATION

STPP Information on status: patent application and granting procedure in general

Free format text: NON FINAL ACTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: RESPONSE TO NON-FINAL OFFICE ACTION ENTERED AND FORWARDED TO EXAMINER

STPP Information on status: patent application and granting procedure in general

Free format text: FINAL REJECTION MAILED

STCB Information on status: application discontinuation

Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION