WO2015105024A1 - チタン粉末材料、チタン素材及び酸素固溶チタン粉末材料の製造方法 - Google Patents
チタン粉末材料、チタン素材及び酸素固溶チタン粉末材料の製造方法 Download PDFInfo
- Publication number
- WO2015105024A1 WO2015105024A1 PCT/JP2014/084529 JP2014084529W WO2015105024A1 WO 2015105024 A1 WO2015105024 A1 WO 2015105024A1 JP 2014084529 W JP2014084529 W JP 2014084529W WO 2015105024 A1 WO2015105024 A1 WO 2015105024A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- titanium
- oxygen
- titanium powder
- oxide film
- powder material
- Prior art date
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
- B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
-
- 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
- B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
- B22F1/102—Metallic powder coated with organic material
-
- 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
- B22F1/12—Metallic powder containing non-metallic 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
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/14—Treatment of metallic powder
- B22F1/142—Thermal or thermo-mechanical 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
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/16—Metallic particles coated with a non-metal
-
- 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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/16—Making metallic powder or suspensions thereof using chemical processes
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/10—Oxidising
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/80—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
- B22F2201/00—Treatment under specific atmosphere
- B22F2201/03—Oxygen
-
- 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
- B22F2201/00—Treatment under specific atmosphere
- B22F2201/10—Inert gases
- B22F2201/11—Argon
-
- 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
- B22F2302/00—Metal Compound, non-Metallic compound or non-metal composition of the powder or its coating
- B22F2302/25—Oxide
-
- 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
Definitions
- the present invention relates to a titanium powder material and a titanium material, and more particularly to a high-strength titanium powder material in which oxygen is dissolved, a titanium material, and a method for producing them.
- Titanium is a lightweight material with a specific gravity about half that of steel, and has excellent corrosion resistance and strength. Therefore, titanium, parts for aircraft, railway vehicles, motorcycles, automobiles, It is used for household appliances and building materials. It is also used as a medical material from the viewpoint of excellent corrosion resistance.
- titanium is used for a limited purpose because of its high material cost compared to steel materials and aluminum alloys.
- a titanium alloy has a high tensile strength exceeding 1000 MPa, but has a problem that ductility (breaking elongation) is not sufficient and plastic workability at room temperature or low temperature is poor.
- pure titanium has a high elongation at break exceeding 25% at room temperature and is excellent in plastic workability in a low temperature range, but has a low tensile strength of about 400 to 600 MPa. is there.
- Patent Document 1 proposes the following steps as a method for obtaining an oxygen solid solution titanium material.
- a step of preparing titanium powder and TiO 2 particles A step of adjusting the added amount of TiO 2 particles to 0.5% to 3.0% on a mass basis with respect to the entire mixed powder and mixing the titanium powder and TiO 2 particles.
- C Step of sintering the above mixture in a temperature range from 700 ° C. to less than the melting point of TiO 2 in a vacuum atmosphere to thermally decompose the TiO 2 particles, and dissociating the dissociated oxygen atoms in titanium. .
- the titanium material produced by the method disclosed in JP2012-241241, that is, the powder metallurgy method using TiO 2 particles, can maintain high strength and high ductility as compared with the melt-processed material. is there.
- the TiO 2 particles have a small particle size, it is easy to make an aggregate. Specifically, when the amount of TiO 2 particles added is increased, aggregates of TiO 2 particles are formed, and the decomposition of TiO 2 does not proceed completely, and the remaining TiO 2 particles start from breaking. As a result, ductility is reduced.
- An object of the present invention is to provide a method for producing an oxygen solid solution titanium powder material capable of dissolving a large amount of oxygen in the titanium powder material while maintaining proper ductility.
- Another object of the present invention is to provide a titanium powder material and a titanium material in which a large amount of oxygen is dissolved while maintaining proper ductility.
- the manufacturing method of the oxygen solid solution titanium powder material according to the present invention includes the following steps.
- B) The titanium powder material having the titanium oxide film is heated in an oxygen-free atmosphere to decompose the titanium oxide film formed on the surface of each titanium powder particle, and the dissociated oxygen atoms are A step of dissolving in a matrix of titanium powder particles.
- the amount of oxygen solid solution in the matrix of each titanium powder particle is increased by performing a plurality of cycles with the formation of the titanium oxide film and the subsequent decomposition of the titanium oxide film as one cycle.
- the heating temperature for forming the titanium oxide film is preferably 160 ° C. or higher and lower than 600 ° C., and the heating temperature for decomposing the titanium oxide film is preferably 450 ° C. or higher and below the melting point.
- the heat treatment that contributes to the formation of the titanium oxide film and the decomposition of the titanium oxide film is preferably carried out by containing the titanium powder material in a rotary kiln heating furnace.
- each titanium powder particle has an oxide film formed naturally in the atmosphere on the surface, and the amount of oxygen dissolved in the matrix of each titanium powder particle is greater than the amount of oxygen in the naturally formed oxide film. There are also many.
- the oxygen content of each titanium powder particle is preferably 0.4% to 4.7%, more preferably 1.15 to 1.9% on a mass basis.
- the titanium powder particles constituting the titanium powder material are made of pure titanium, and the average value of the micro Vickers hardness of the matrix of the titanium powder particles is 200 to 600.
- a titanium material molded into a predetermined shape using the oxygen solid solution titanium powder material described above is also an object of the present invention.
- the titanium material is a pure Ti powder extruded material, the oxygen content with respect to the whole extruded material is 1.2% by mass or more, and the elongation at break is 18% or more.
- FIG. 1 is a diagram schematically showing the features of the present invention. First, the outline of the invention will be described with reference to FIG. 1, and more detailed data will be described thereafter.
- titanium powder material A titanium powder material consisting of a large number of titanium powder particles is prepared.
- titanium powder particles may be either pure titanium powder particles or titanium alloy powder particles.
- Each titanium powder particle has an oxide film (natural oxide film) formed naturally in the atmosphere on the surface, but is a very thin film, and therefore the natural oxide film is not shown in FIG.
- the natural oxide film has a thickness of about 0.1 to 1 ⁇ m.
- the prepared titanium powder material is heated in an atmosphere containing oxygen to form a titanium oxide film on the surface of each titanium powder particle.
- the heat treatment that contributes to the formation of the titanium oxide film is preferably carried out by containing the titanium powder material in a rotary kiln heating furnace.
- the heating conditions are, for example, as follows.
- Heating atmosphere 10 vol. % O 2 -90 vol. % Ar mixed gas Mixed gas flow rate: 1 L / min. Heating temperature: 200 ° C Holding time: 30 min. Rotational speed: 20 rpm.
- the titanium oxide film is formed on the surface of each titanium powder particle by the above oxidation heat treatment.
- the reason why the rotary kiln heating furnace is used is to prevent titanium powder particles from being pre-sintered into a lump during oxidation heat treatment by applying rotation or vibration to the titanium powder material.
- the reason why argon gas is included is to prevent abnormal heat generation of the titanium powder material due to excessive oxygen.
- Titanium powder material having a titanium oxide film on its surface is heated in an oxygen-free atmosphere to decompose the titanium oxide film formed on the surface of each titanium powder particle, and the dissociated oxygen atoms are separated from each titanium powder. Solid solution in the matrix of particles.
- the heat treatment that contributes to the decomposition of the titanium oxide film is preferably carried out by accommodating the titanium powder material in a rotary kiln heating furnace.
- the oxidation heat treatment and solution heat treatment described above may be performed using the same rotary kiln heating furnace.
- the heating conditions are, for example, as follows.
- Heating atmosphere 100 vol. % Ar gas Gas flow rate: 1 L / min. Heating temperature: 600 ° C Holding time: 30 min. Or 60 min. Rotational speed: 20 rpm.
- the oxygen solution generated by the decomposition of the titanium oxide film is uniformly diffused into the matrix of each titanium powder particle by the above solution heat treatment and is dissolved. In this way, the target oxygen solid solution titanium powder material can be obtained.
- the oxygen-dissolved titanium powder material obtained as described above When the oxygen-dissolved titanium powder material obtained as described above is placed in the atmosphere, a natural oxide film is formed on the surface of each titanium powder particle.
- the amount of oxygen in the natural oxide film is at most about 0.2% by mass with respect to the entire titanium powder particles.
- the oxidation heat treatment and the solution heat treatment are performed by the method of the present invention, the amount of oxygen dissolved in the matrix of each titanium powder particle becomes larger than the amount of oxygen in the natural oxide film.
- FIG. 2 is a graph showing changes in the diffraction peak of Ti when pure titanium raw material powder is subjected to oxidation heat treatment and solution heat treatment.
- the Ti diffraction peak shifts to the low angle side, and when the solution heat treatment is further performed, the Ti diffraction peak significantly decreases to the low angle side. It is recognized that there is a shift.
- These peak shifts indicate that oxygen atoms were dissolved in the Ti substrate (matrix).
- a large amount of oxygen atoms contribute to the formation of the titanium oxide film, and a few oxygen atoms are dissolved in the Ti substrate. It can be seen that during the solution heat treatment, the titanium oxide film is decomposed and a large amount of oxygen atoms are dissolved in the Ti substrate.
- FIG. 3 is a diagram showing a change in the diffraction peak of TiO 2 when an oxidation heat treatment and a solution heat treatment are performed on a pure titanium raw material powder.
- a slight diffraction peak of TiO 2 is detected in the pure titanium raw material powder. This is because the pure titanium raw material powder has an oxide film (natural oxide film) formed naturally in the atmosphere. Since the titanium oxide film is formed on the powder particle surface during the oxidation heat treatment, the peak intensity of TiO 2 is high.
- the solution heat treatment it is recognized that the titanium oxide film is thermally decomposed and oxygen atoms are dissolved in the Ti base material, so that the TiO 2 peak disappears.
- Oxidative heat treatment heating atmosphere 10% O 2 + 90% Ar mixed gas (flow rate: 1 L / min.) Heating temperature: 200 ° C Holding time: 30 min. Rotational speed: 20 rpm. Solution heat treatment heating atmosphere: 100% Ar gas (flow rate: 1 L / min.) Heating temperature: 600 ° C Holding time: 30 min. Rotational speed: 20 rpm.
- the measurement results are shown in Table 1 and FIG.
- the column of the number of repetitions 0 is the oxygen amount and nitrogen amount of the pure titanium powder before the heat treatment. Oxygen is mainly contained in the natural oxide film.
- the oxygen content increases linearly in proportion to the number of repetitions of the above cycle, while the nitrogen content remains constant without change.
- the oxygen content of the titanium powder particles is increased to nearly 4.7%.
- the pure titanium raw material powder was subjected to an oxidation heat treatment, and further subjected to a solution heat treatment to measure how the micro Vickers hardness (Hv) changes.
- the measured sample was subjected to one cycle of oxidation heat treatment and solution heat treatment, and the oxygen content after the solution heat treatment was 1.18% by mass.
- the oxygen content in the Ti powder increases by increasing the number of cycles of oxidation / solution heat treatment.
- an extremely hard Ti powder having a substrate hardness exceeding 600 Hv requires high pressure when compression molding it, and at the same time, the powder becomes brittle and cracks are generated inside the powder molded body. A molded product cannot be obtained.
- the hardness of the pure Ti powder subjected to the oxidation / solution heat treatment according to the present invention is 200 to 600 Hv.
- Example 1 Pure Ti powder (average particle size: 28 ⁇ m, purity> 95%) is used as a starting material, and the oxidation heat treatment and solution heat treatment shown below are set as one cycle, and this is repeated up to 4 times to produce oxygen solid solution pure Ti powder. did.
- Oxidation heat treatment atmosphere 10% O 2 + 90% Ar mixed gas Temperature: 200 ° C. Holding time: 15 minutes Number of rotations: 20 rpm. Solution heat treatment atmosphere: 100% Ar gas Temperature: 600 ° C. Holding time: 30 minutes Number of rotations: 20 rpm.
- the oxygen content of each extruded material was analyzed and a tensile test was performed at room temperature to measure the tensile strength, proof stress, and elongation at break, and the dependency on the oxygen content was investigated.
- Table 3 shows the measurement results.
- FIG. 6 shows the comparison of tensile strength
- FIG. 7 shows the comparison of proof stress.
- the production method (direct oxidation solution heat treatment) according to the present invention, as the oxygen content increases, the tensile strength (UTS) and the yield strength (YS) both increase almost linearly, while the breaking elongation ( ⁇ ). However, it exhibited a sufficiently good ductility of 18.1% at an oxygen content of 1.66% by mass.
- a sample having an oxygen content of 0.21% by mass is an extruded material composed of pure titanium powder particles in which oxygen is not solid-solved, and is in the natural oxide film formed on the surface of each particle. It means that the amount of oxygen is about 0.21% by mass.
- the oxygen content of the sample subjected to the direct oxidation solution heat treatment is 0.42% or more.
- the material having an oxygen content of 1.24% by mass in the pure Ti powder extruded material by direct oxidation solution heat treatment and the oxygen content of 1.23% by mass in the pure Ti powder extruded material by adding TiO 2 particles The fracture starting point of the fracture surface after the tensile test with the material was observed with a scanning electron microscope (SEM). A photomicrograph is shown in FIG.
- fine dimples are confirmed and a uniform ductile fracture surface is exhibited.
- the material produced by the TiO 2 particle addition the presence of TiO 2 particles unreacted was observed at the origin of the fracture. That is, since the TiO 2 particles aggregated in the state of the Ti + TiO 2 mixed powder, unreacted TiO 2 became the starting point of fracture, and as a result, the elongation at break was significantly reduced.
- Example 2 The effect of heating temperature during oxidative heat treatment was investigated. Using the same pure Ti powder as before, 50 g of Ti powder was heated to a rotary kiln-type heat treatment furnace with oxygen + argon mixed gas (10% O 2 + 90% Ar / flow rate: 1 L / min.) Flowing at a heating temperature of 100 Ti powder was produced by changing the temperature to ⁇ 700 ° C. Note that the holding time at each temperature in the oxidation heat treatment is 1 hr, and the rotational speed is 20 rpm. It was.
- the temperature range suitable for the oxidation heat treatment of the Ti powder is 160 ° C. or more, and the oxidation heat treatment at less than 600 ° C. is effective for suppressing the partial melting of the Ti powder.
- Example 3 The influence of heating temperature during solution heat treatment was investigated.
- the oxidation heat treatment under the following conditions was performed on the pure Ti powder as before.
- Heating atmosphere 10% O 2 + 90% Ar mixed gas (flow rate: 1 L / min.) Heating temperature: 200 ° C Holding time: 30 min. Rotational speed: 20 rpm.
- the heating temperature was changed in the range of 300 to 800 ° C. in an argon gas atmosphere to produce Ti powder.
- the holding time at each temperature in the solution heat treatment was 1 hr, the argon gas flow rate: 1 L / min, and the rotation speed: 20 rpm.
- the weight of Ti powder to be charged into the heating furnace at one time was set to two conditions of 30 g and 150 g, and the influence of the input amount during the heat treatment was also investigated.
- heat treatment at 450 ° C. or higher is required to thermally decompose the oxide film TiO 2 formed by oxidation heat treatment and to dissolve oxygen atoms in the Ti substrate.
- a higher temperature of 550 ° C. or higher is desirable to stably and uniformly dissolve oxygen atoms completely.
- the present invention can be advantageously used to obtain a high-strength titanium powder material and a titanium material in which a large amount of oxygen is dissolved while maintaining proper ductility.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Materials Engineering (AREA)
- Organic Chemistry (AREA)
- Thermal Sciences (AREA)
- Physics & Mathematics (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Manufacturing & Machinery (AREA)
- General Chemical & Material Sciences (AREA)
- Powder Metallurgy (AREA)
- Inorganic Compounds Of Heavy Metals (AREA)
Abstract
Description
(a)チタン粉末とTiO2粒子とを準備する工程。
(b)混合粉末全体に対してTiO2粒子の添加量が質量基準で0.5%~3.0%となるように調整してチタン粉末とTiO2粒子とを混合する工程。
(c)上記の混合物を、700℃からTiO2の融点未満の温度範囲で、かつ真空雰囲気中で焼結してTiO2粒子を熱分解させ、解離した酸素原子をチタン中に固溶させる工程。
(a)チタン粉末粒子からなるチタン粉末材料を、酸素を含む雰囲気中で加熱して上記チタン粉末粒子の表面にチタン酸化皮膜を形成する工程。
(b)上記チタン酸化皮膜を有するチタン粉末材料を、酸素を含まない雰囲気中で加熱して各チタン粉末粒子の表面に形成されたチタン酸化皮膜を分解し、その際に解離した酸素原子を各チタン粉末粒子のマトリクス中に固溶させる工程。
上記の特徴的な構成の作用効果または技術的意義については、以下の項目で説明する。
多数のチタン粉末粒子からなるチタン粉末材料を準備する。ここで「チタン粉末粒子」とは、純チタン粉末粒子またチタン合金粉末粒子のいずれであってもよい。各チタン粉末粒子は、大気中で自然に形成された酸化膜(自然酸化膜)を表面に有しているが、非常に薄い膜であるので、図1では自然酸化膜を図示していない。自然酸化膜の厚みは、0.1~1μm程度である。
準備したチタン粉末材料を、酸素を含む雰囲気中で加熱して各チタン粉末粒子の表面にチタン酸化皮膜を形成する。チタン酸化皮膜の形成に資する熱処理は、好ましくは、チタン粉末材料をロータリーキルン式加熱炉内に収容して行う。加熱条件は、例えば、以下の通りである。
混合ガス流量:1L/min.
加熱温度:200℃
保持時間:30min.
回転数:20rpm.
表面にチタン酸化皮膜を有するチタン粉末材料を、酸素を含まない雰囲気中で加熱して各チタン粉末粒子の表面に形成されたチタン酸化皮膜を分解し、その際に解離した酸素原子を各チタン粉末粒子のマトリクス中に固溶させる。チタン酸化皮膜の分解に資する熱処理は、好ましくは、チタン粉末材料をロータリーキルン式加熱炉内に収容して行う。前述した酸化熱処理および固溶化熱処理を同一のロータリーキルン式加熱炉を用いて行ってもよい。加熱条件は、例えば、以下の通りである。
ガス流量:1L/min.
加熱温度:600℃
保持時間:30min.または60min.
回転数:20rpm.
酸化熱処理の時間を増大しても酸素固溶量は増加しない。その理由は、チタン粉末粒子表面に形成されるチタン酸化皮膜がバリアとなり、更なる酸化反応が進行しないからである。チタン粉末粒子のマトリクス中に固溶する酸素の量を増加するには、酸化熱処理時間を増やすのではなく、チタン酸化皮膜形成のための酸化熱処理、および引き続いてのチタン酸化皮膜分解のための固溶化熱処理を1サイクルとして複数回のサイクルを行うことが望ましい。
図2は、純チタン原料粉末に対して酸化熱処理および固溶化熱処理を行った場合のTiの回折ピークの変化を示す図である。図2から明らかなように、純チタン原料粉末に対して酸化熱処理を行うとTiの回折ピークが低角度側にシフトし、さらに固溶化熱処理を行うとTiの回折ピークが顕著に低角度側にシフトしていることが認められる。これらのピークのシフトは、Tiの素地(マトリクス)中に酸素原子が固溶したことを示すものである。酸化熱処理時には、多量の酸素原子がチタン酸化皮膜の形成に寄与し、僅かの酸素原子がTiの素地中に固溶する。固溶化熱処理時には、チタン酸化皮膜が分解し、多量の酸素原子がTiの素地中に固溶していることがわかる。
下記の条件の酸化熱処理および固溶化熱処理を1サイクルとし、このサイクルを4回繰り返して純チタン粉末中の酸素量および窒素量を測定した。使用した純チタン粉末は、平均粒子径が28μm、純度が95%を超えるものであった。
加熱雰囲気:10%O2+90%Ar混合ガス(流量:1L/min.)
加熱温度:200℃
保持時間:30min.
回転数:20rpm.
固溶化熱処理
加熱雰囲気:100%Arガス(流量:1L/min.)
加熱温度:600℃
保持時間:30min.
回転数:20rpm.
純チタン原料粉末に対して、酸化熱処理を行い、さらに固溶化熱処理を行って、マイクロビッカース硬さ(Hv)がどのように変化するかを測定した。測定した試料は、酸化熱処理および固溶化熱処理のサイクルを1回施したものであり、固溶化熱処理後の酸素含有量が1.18質量%になるものであった。
純Ti粉末(平均粒子径;28μm、純度>95%)を出発原料とし、下記に示す酸化熱処理および固溶化熱処理を1サイクルとし、これを最高4回まで繰り返して酸素固溶純Ti粉末を作製した。
雰囲気:10%O2+90%Ar混合ガス
温度:200℃
保持時間:15分
回転数:20rpm.
固溶化熱処理
雰囲気:100%Arガス
温度:600℃
保持時間:30分
回転数:20rpm.
酸化熱処理時の加熱温度の影響を調査した。これまでと同様の純Ti粉末を用いて、ロータリーキルン式熱処理炉に酸素+アルゴン混合ガス(10%O2+90%Ar/流量;1L/min.)を流入した状態でTi粉末50gを加熱温度100~700℃に変化させてTi粉末を作製した。なお、酸化熱処理における各温度での保持時間はいずれも1hrとし、回転数を20rpm.とした。
固溶化熱処理時の加熱温度の影響を調査した。これまでと同様に純Ti粉末に対して、下記の条件の酸化熱処理を行った。
加熱温度:200℃
保持時間:30min.
回転数:20rpm.
Claims (10)
- チタン粉末粒子からなるチタン粉末材料を、酸素を含む雰囲気中で加熱して前記粉末粒子の表面にチタン酸化皮膜を形成する工程と、
前記チタン酸化皮膜を有する前記チタン粉末材料を、酸素を含まない雰囲気中で加熱して前記各チタン粉末粒子の表面に形成されたチタン酸化皮膜を分解し、その際に解離した酸素原子を前記各チタン粉末粒子のマトリクス中に固溶させる工程と、を備える、酸素固溶チタン粉末材料の製造方法。 - 前記チタン酸化皮膜の形成および引き続いての前記チタン酸化皮膜の分解を1サイクルとして複数回のサイクルを行うことによって、前記各チタン粉末粒子のマトリクス中への酸素固溶量を増加する、請求項1に記載の酸素固溶チタン粉末材料の製造方法。
- 前記チタン酸化皮膜を形成するための加熱温度は、160℃以上600℃未満であり、
前記チタン酸化皮膜を分解するための加熱温度は、450℃以上で融点以下である、請求項1または2に記載の酸素固溶チタン粉末材料の製造方法。 - 前記チタン酸化皮膜の形成およびチタン酸化皮膜の分解に資する熱処理は、前記チタン粉末材料をロータリーキルン式加熱炉内に収容して行う、請求項1~3のいずれかに記載の酸素固溶チタン粉末材料の製造方法。
- 請求項1~4のいずれかに記載の方法によって製造された酸素固溶チタン粉末材料であって、
前記各チタン粉末粒子は、大気中で自然に形成された酸化膜を表面に有しており、
前記各チタン粉末粒子のマトリクス中に固溶した酸素量は、前記自然形成酸化膜中の酸素量よりも多いことを特徴とする、酸素固溶チタン粉末材料。 - 前記各チタン粉末粒子の酸素含有量は、質量基準で、0.4%~4.7%である、請求項5に記載の酸素固溶チタン粉末材料。
- 前記各チタン粉末粒子の酸素含有量は、質量基準で、1.15~1.9%である、請求項6に記載の酸素固溶チタン粉末材料。
- 前記チタン粉末粒子は純チタンからなり、
前記チタン粉末粒子のマトリクスのマイクロビッカース硬さの平均値は、200~600である、請求項5~7のいずれかに記載の酸素固溶チタン粉末材料。 - 請求項5~8のいずれかに記載の酸素固溶チタン粉末材料を用いて所定の形状に成形したチタン素材。
- 当該チタン素材は純Ti粉末押出材であり、
押出材全体に対する酸素含有量が1.2質量%以上であり、
破断伸びが18%以上である、請求項9に記載のチタン素材。
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2015556775A JP6054553B2 (ja) | 2014-01-10 | 2014-12-26 | 酸素固溶チタン素材、酸素固溶チタン粉末材料及び酸素固溶チタン粉末材料の製造方法 |
CN201480072562.5A CN105899314B (zh) | 2014-01-10 | 2014-12-26 | 钛粉末材料、钛材以及氧固溶钛粉末材料的制备方法 |
US15/110,551 US10307824B2 (en) | 2014-01-10 | 2014-12-26 | Titanium powder, titanium material, and method for producing titanium powder containing solid-soluted oxygen |
EP14877708.9A EP3093085B1 (en) | 2014-01-10 | 2014-12-26 | Method for producing oxygen solid solution titanium powder material |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2014003392 | 2014-01-10 | ||
JP2014-003392 | 2014-01-10 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2015105024A1 true WO2015105024A1 (ja) | 2015-07-16 |
Family
ID=53523857
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2014/084529 WO2015105024A1 (ja) | 2014-01-10 | 2014-12-26 | チタン粉末材料、チタン素材及び酸素固溶チタン粉末材料の製造方法 |
Country Status (5)
Country | Link |
---|---|
US (1) | US10307824B2 (ja) |
EP (1) | EP3093085B1 (ja) |
JP (1) | JP6054553B2 (ja) |
CN (1) | CN105899314B (ja) |
WO (1) | WO2015105024A1 (ja) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2018104778A (ja) * | 2016-12-27 | 2018-07-05 | 勝義 近藤 | 焼結刃物素材およびその製造方法 |
WO2022202740A1 (ja) * | 2021-03-26 | 2022-09-29 | 国立研究開発法人物質・材料研究機構 | 超臨界水利用装置用チタン合金 |
WO2024077526A1 (zh) * | 2022-10-12 | 2024-04-18 | 清华大学 | 纯钛制件及其制备方法 |
Families Citing this family (77)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
ES2770053T3 (es) | 2014-05-16 | 2020-06-30 | Divergent Tech Inc | Nodos formados modulares para chasis de vehículo y sus métodos de uso |
EP3164260B1 (en) | 2014-07-02 | 2021-07-28 | Divergent Technologies, Inc. | Vehicle chassis |
JP2019527138A (ja) | 2016-06-09 | 2019-09-26 | ダイバージェント テクノロジーズ, インコーポレイテッドDivergent Technologies, Inc. | アークおよびノードの設計ならびに製作のためのシステムおよび方法 |
US10759090B2 (en) | 2017-02-10 | 2020-09-01 | Divergent Technologies, Inc. | Methods for producing panels using 3D-printed tooling shells |
US11155005B2 (en) | 2017-02-10 | 2021-10-26 | Divergent Technologies, Inc. | 3D-printed tooling and methods for producing same |
US10898968B2 (en) | 2017-04-28 | 2021-01-26 | Divergent Technologies, Inc. | Scatter reduction in additive manufacturing |
US10703419B2 (en) | 2017-05-19 | 2020-07-07 | Divergent Technologies, Inc. | Apparatus and methods for joining panels |
US11358337B2 (en) | 2017-05-24 | 2022-06-14 | Divergent Technologies, Inc. | Robotic assembly of transport structures using on-site additive manufacturing |
US11123973B2 (en) | 2017-06-07 | 2021-09-21 | Divergent Technologies, Inc. | Interconnected deflectable panel and node |
US10919230B2 (en) | 2017-06-09 | 2021-02-16 | Divergent Technologies, Inc. | Node with co-printed interconnect and methods for producing same |
US10781846B2 (en) | 2017-06-19 | 2020-09-22 | Divergent Technologies, Inc. | 3-D-printed components including fasteners and methods for producing same |
US10994876B2 (en) | 2017-06-30 | 2021-05-04 | Divergent Technologies, Inc. | Automated wrapping of components in transport structures |
US11022375B2 (en) | 2017-07-06 | 2021-06-01 | Divergent Technologies, Inc. | Apparatus and methods for additively manufacturing microtube heat exchangers |
US10895315B2 (en) | 2017-07-07 | 2021-01-19 | Divergent Technologies, Inc. | Systems and methods for implementing node to node connections in mechanized assemblies |
US10751800B2 (en) | 2017-07-25 | 2020-08-25 | Divergent Technologies, Inc. | Methods and apparatus for additively manufactured exoskeleton-based transport structures |
US10940609B2 (en) | 2017-07-25 | 2021-03-09 | Divergent Technologies, Inc. | Methods and apparatus for additively manufactured endoskeleton-based transport structures |
US10605285B2 (en) | 2017-08-08 | 2020-03-31 | Divergent Technologies, Inc. | Systems and methods for joining node and tube structures |
US10357959B2 (en) | 2017-08-15 | 2019-07-23 | Divergent Technologies, Inc. | Methods and apparatus for additively manufactured identification features |
US11306751B2 (en) | 2017-08-31 | 2022-04-19 | Divergent Technologies, Inc. | Apparatus and methods for connecting tubes in transport structures |
US10960611B2 (en) | 2017-09-06 | 2021-03-30 | Divergent Technologies, Inc. | Methods and apparatuses for universal interface between parts in transport structures |
US11292058B2 (en) | 2017-09-12 | 2022-04-05 | Divergent Technologies, Inc. | Apparatus and methods for optimization of powder removal features in additively manufactured components |
US10668816B2 (en) | 2017-10-11 | 2020-06-02 | Divergent Technologies, Inc. | Solar extended range electric vehicle with panel deployment and emitter tracking |
US10814564B2 (en) | 2017-10-11 | 2020-10-27 | Divergent Technologies, Inc. | Composite material inlay in additively manufactured structures |
US11786971B2 (en) | 2017-11-10 | 2023-10-17 | Divergent Technologies, Inc. | Structures and methods for high volume production of complex structures using interface nodes |
US10926599B2 (en) | 2017-12-01 | 2021-02-23 | Divergent Technologies, Inc. | Suspension systems using hydraulic dampers |
US11110514B2 (en) | 2017-12-14 | 2021-09-07 | Divergent Technologies, Inc. | Apparatus and methods for connecting nodes to tubes in transport structures |
US11085473B2 (en) | 2017-12-22 | 2021-08-10 | Divergent Technologies, Inc. | Methods and apparatus for forming node to panel joints |
US11534828B2 (en) | 2017-12-27 | 2022-12-27 | Divergent Technologies, Inc. | Assembling structures comprising 3D printed components and standardized components utilizing adhesive circuits |
US11420262B2 (en) | 2018-01-31 | 2022-08-23 | Divergent Technologies, Inc. | Systems and methods for co-casting of additively manufactured interface nodes |
US10751934B2 (en) | 2018-02-01 | 2020-08-25 | Divergent Technologies, Inc. | Apparatus and methods for additive manufacturing with variable extruder profiles |
US11224943B2 (en) | 2018-03-07 | 2022-01-18 | Divergent Technologies, Inc. | Variable beam geometry laser-based powder bed fusion |
US11267236B2 (en) | 2018-03-16 | 2022-03-08 | Divergent Technologies, Inc. | Single shear joint for node-to-node connections |
US11254381B2 (en) | 2018-03-19 | 2022-02-22 | Divergent Technologies, Inc. | Manufacturing cell based vehicle manufacturing system and method |
US11872689B2 (en) | 2018-03-19 | 2024-01-16 | Divergent Technologies, Inc. | End effector features for additively manufactured components |
US11408216B2 (en) | 2018-03-20 | 2022-08-09 | Divergent Technologies, Inc. | Systems and methods for co-printed or concurrently assembled hinge structures |
US11613078B2 (en) | 2018-04-20 | 2023-03-28 | Divergent Technologies, Inc. | Apparatus and methods for additively manufacturing adhesive inlet and outlet ports |
US11214317B2 (en) | 2018-04-24 | 2022-01-04 | Divergent Technologies, Inc. | Systems and methods for joining nodes and other structures |
US10682821B2 (en) | 2018-05-01 | 2020-06-16 | Divergent Technologies, Inc. | Flexible tooling system and method for manufacturing of composite structures |
US11020800B2 (en) | 2018-05-01 | 2021-06-01 | Divergent Technologies, Inc. | Apparatus and methods for sealing powder holes in additively manufactured parts |
US11389816B2 (en) | 2018-05-09 | 2022-07-19 | Divergent Technologies, Inc. | Multi-circuit single port design in additively manufactured node |
US10691104B2 (en) | 2018-05-16 | 2020-06-23 | Divergent Technologies, Inc. | Additively manufacturing structures for increased spray forming resolution or increased fatigue life |
US11590727B2 (en) | 2018-05-21 | 2023-02-28 | Divergent Technologies, Inc. | Custom additively manufactured core structures |
US11441586B2 (en) | 2018-05-25 | 2022-09-13 | Divergent Technologies, Inc. | Apparatus for injecting fluids in node based connections |
US11035511B2 (en) | 2018-06-05 | 2021-06-15 | Divergent Technologies, Inc. | Quick-change end effector |
CN108569861A (zh) * | 2018-07-05 | 2018-09-25 | 安徽思凯瑞环保科技有限公司 | 抗潮解的粗钛粉及其制备方法 |
US11292056B2 (en) | 2018-07-06 | 2022-04-05 | Divergent Technologies, Inc. | Cold-spray nozzle |
US11269311B2 (en) | 2018-07-26 | 2022-03-08 | Divergent Technologies, Inc. | Spray forming structural joints |
US10836120B2 (en) | 2018-08-27 | 2020-11-17 | Divergent Technologies, Inc . | Hybrid composite structures with integrated 3-D printed elements |
US11433557B2 (en) | 2018-08-28 | 2022-09-06 | Divergent Technologies, Inc. | Buffer block apparatuses and supporting apparatuses |
US11826953B2 (en) | 2018-09-12 | 2023-11-28 | Divergent Technologies, Inc. | Surrogate supports in additive manufacturing |
US11072371B2 (en) | 2018-10-05 | 2021-07-27 | Divergent Technologies, Inc. | Apparatus and methods for additively manufactured structures with augmented energy absorption properties |
US11260582B2 (en) | 2018-10-16 | 2022-03-01 | Divergent Technologies, Inc. | Methods and apparatus for manufacturing optimized panels and other composite structures |
US11504912B2 (en) | 2018-11-20 | 2022-11-22 | Divergent Technologies, Inc. | Selective end effector modular attachment device |
USD911222S1 (en) | 2018-11-21 | 2021-02-23 | Divergent Technologies, Inc. | Vehicle and/or replica |
US11529741B2 (en) | 2018-12-17 | 2022-12-20 | Divergent Technologies, Inc. | System and method for positioning one or more robotic apparatuses |
US11449021B2 (en) | 2018-12-17 | 2022-09-20 | Divergent Technologies, Inc. | Systems and methods for high accuracy fixtureless assembly |
US10663110B1 (en) | 2018-12-17 | 2020-05-26 | Divergent Technologies, Inc. | Metrology apparatus to facilitate capture of metrology data |
US11885000B2 (en) | 2018-12-21 | 2024-01-30 | Divergent Technologies, Inc. | In situ thermal treatment for PBF systems |
US11203240B2 (en) | 2019-04-19 | 2021-12-21 | Divergent Technologies, Inc. | Wishbone style control arm assemblies and methods for producing same |
US11912339B2 (en) | 2020-01-10 | 2024-02-27 | Divergent Technologies, Inc. | 3-D printed chassis structure with self-supporting ribs |
US11590703B2 (en) | 2020-01-24 | 2023-02-28 | Divergent Technologies, Inc. | Infrared radiation sensing and beam control in electron beam additive manufacturing |
US11479015B2 (en) | 2020-02-14 | 2022-10-25 | Divergent Technologies, Inc. | Custom formed panels for transport structures and methods for assembling same |
US11884025B2 (en) | 2020-02-14 | 2024-01-30 | Divergent Technologies, Inc. | Three-dimensional printer and methods for assembling parts via integration of additive and conventional manufacturing operations |
US11421577B2 (en) | 2020-02-25 | 2022-08-23 | Divergent Technologies, Inc. | Exhaust headers with integrated heat shielding and thermal syphoning |
US11535322B2 (en) | 2020-02-25 | 2022-12-27 | Divergent Technologies, Inc. | Omni-positional adhesion device |
JP7383524B2 (ja) * | 2020-02-27 | 2023-11-20 | 東邦チタニウム株式会社 | 多孔質金属体の製造方法及び、多孔質金属体 |
US11413686B2 (en) | 2020-03-06 | 2022-08-16 | Divergent Technologies, Inc. | Methods and apparatuses for sealing mechanisms for realizing adhesive connections with additively manufactured components |
US11850804B2 (en) | 2020-07-28 | 2023-12-26 | Divergent Technologies, Inc. | Radiation-enabled retention features for fixtureless assembly of node-based structures |
CN112048638B (zh) * | 2020-07-29 | 2022-04-22 | 北京科技大学 | 钛基合金粉末及制备方法、钛基合金制件的制备方法 |
US11806941B2 (en) | 2020-08-21 | 2023-11-07 | Divergent Technologies, Inc. | Mechanical part retention features for additively manufactured structures |
US12083596B2 (en) | 2020-12-21 | 2024-09-10 | Divergent Technologies, Inc. | Thermal elements for disassembly of node-based adhesively bonded structures |
US11872626B2 (en) | 2020-12-24 | 2024-01-16 | Divergent Technologies, Inc. | Systems and methods for floating pin joint design |
US11947335B2 (en) | 2020-12-30 | 2024-04-02 | Divergent Technologies, Inc. | Multi-component structure optimization for combining 3-D printed and commercially available parts |
US11928966B2 (en) | 2021-01-13 | 2024-03-12 | Divergent Technologies, Inc. | Virtual railroad |
WO2022192465A1 (en) | 2021-03-09 | 2022-09-15 | Divergent Technologies, Inc. | Rotational additive manufacturing systems and methods |
US12090551B2 (en) | 2021-04-23 | 2024-09-17 | Divergent Technologies, Inc. | Removal of supports, and other materials from surface, and within hollow 3D printed parts |
US11865617B2 (en) | 2021-08-25 | 2024-01-09 | Divergent Technologies, Inc. | Methods and apparatuses for wide-spectrum consumption of output of atomization processes across multi-process and multi-scale additive manufacturing modalities |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2002077305A1 (fr) * | 2001-03-26 | 2002-10-03 | Kabushiki Kaisha Toyota Chuo Kenkyusho | Alliage de titane a haute resistance et son procede de production |
JP2006342401A (ja) * | 2005-06-09 | 2006-12-21 | National Institute For Materials Science | 高温制振性を有するβ型チタン合金 |
JP2012241241A (ja) | 2011-05-20 | 2012-12-10 | Katsuyoshi Kondo | チタン材料およびその製造方法 |
Family Cites Families (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2584551B2 (ja) | 1991-06-28 | 1997-02-26 | 日本鋼管株式会社 | チタン材の表面硬化処理方法 |
JP2793958B2 (ja) * | 1993-06-25 | 1998-09-03 | 川崎製鉄株式会社 | 金属粉末射出成形法によるチタン系焼結体の製造方法 |
JP3569019B2 (ja) | 1995-02-23 | 2004-09-22 | シチズン時計株式会社 | 粉末射出成形用組成物およびその製造方法 |
DE69730133T2 (de) * | 1996-03-26 | 2004-12-09 | Citizen Watch Co., Ltd., Nishitokyo | Titan oder titanlegierung und oberflächenbehandlungsverfahren dafür |
JP4408184B2 (ja) | 2001-03-26 | 2010-02-03 | 株式会社豊田中央研究所 | チタン合金およびその製造方法 |
CN101254536B (zh) | 2008-04-03 | 2010-08-11 | 北京科技大学 | 利用醋酸钴低温制备钴包覆钛粉的方法 |
CN101758221A (zh) | 2008-11-07 | 2010-06-30 | 南通芯迎设计服务有限公司 | 一种表面包铝二氧化钛粉体的制备方法 |
BR112016016577B1 (pt) | 2014-01-24 | 2021-05-04 | Hi-Lex Corporation | método para a produção de pó de titânio que contém um nitrogênio solubilizado sólido |
-
2014
- 2014-12-26 WO PCT/JP2014/084529 patent/WO2015105024A1/ja active Application Filing
- 2014-12-26 JP JP2015556775A patent/JP6054553B2/ja active Active
- 2014-12-26 CN CN201480072562.5A patent/CN105899314B/zh active Active
- 2014-12-26 EP EP14877708.9A patent/EP3093085B1/en active Active
- 2014-12-26 US US15/110,551 patent/US10307824B2/en active Active
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2002077305A1 (fr) * | 2001-03-26 | 2002-10-03 | Kabushiki Kaisha Toyota Chuo Kenkyusho | Alliage de titane a haute resistance et son procede de production |
JP2006342401A (ja) * | 2005-06-09 | 2006-12-21 | National Institute For Materials Science | 高温制振性を有するβ型チタン合金 |
JP2012241241A (ja) | 2011-05-20 | 2012-12-10 | Katsuyoshi Kondo | チタン材料およびその製造方法 |
Non-Patent Citations (1)
Title |
---|
See also references of EP3093085A4 |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2018104778A (ja) * | 2016-12-27 | 2018-07-05 | 勝義 近藤 | 焼結刃物素材およびその製造方法 |
WO2022202740A1 (ja) * | 2021-03-26 | 2022-09-29 | 国立研究開発法人物質・材料研究機構 | 超臨界水利用装置用チタン合金 |
WO2024077526A1 (zh) * | 2022-10-12 | 2024-04-18 | 清华大学 | 纯钛制件及其制备方法 |
Also Published As
Publication number | Publication date |
---|---|
CN105899314B (zh) | 2017-12-15 |
EP3093085A1 (en) | 2016-11-16 |
EP3093085A4 (en) | 2017-09-20 |
US20160332233A1 (en) | 2016-11-17 |
CN105899314A (zh) | 2016-08-24 |
US10307824B2 (en) | 2019-06-04 |
JPWO2015105024A1 (ja) | 2017-03-23 |
JP6054553B2 (ja) | 2016-12-27 |
EP3093085B1 (en) | 2022-04-27 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP6054553B2 (ja) | 酸素固溶チタン素材、酸素固溶チタン粉末材料及び酸素固溶チタン粉末材料の製造方法 | |
JP6261618B2 (ja) | チタン素材および窒素固溶チタン粉末材料の製造方法 | |
JP5760278B2 (ja) | チタン材料およびその製造方法 | |
Zadra et al. | High-performance, low-cost titanium metal matrix composites | |
EP2394952A2 (en) | Nanoparticles prepared using carbon nanotube and preparation method therefor | |
JP5759426B2 (ja) | チタン合金及びその製造方法 | |
JP5709239B2 (ja) | チタン基複合材料の製造方法および該方法によって製造されたチタン基複合材料 | |
Božić et al. | Synthesis and properties of a Cu–Ti–TiB2 composite hardened by multiple mechanisms | |
WO2013162658A2 (en) | Oxygen-enriched ti-6ai-4v alloy and process for manufacture | |
WO2015157411A1 (en) | Aluminum alloy powder formulations with silicon additions for mechanical property improvements | |
Alshammari et al. | Behaviour of novel low-cost blended elemental Ti–5Fe-xAl alloys fabricated via powder metallurgy | |
WO2017077922A1 (ja) | 酸素固溶チタン焼結体およびその製造方法 | |
US9334550B2 (en) | Method of controlling the carbon or oxygen content of a powder injection | |
Zhu et al. | Influences of carbon additions on reaction mechanisms and tensile properties of Al-based composites synthesized in-situ by Al–SiO2 powder system | |
JP6885900B2 (ja) | Ti−Fe系焼結合金素材およびその製造方法 | |
JP2015178676A (ja) | Ni3Al基Ti−Ni−Al系金属間化合物及びその製造方法 | |
JP2019516021A (ja) | チタンまたはチタン合金にて構成される部材の粉末冶金を用いた製造方法 | |
JP6669471B2 (ja) | 窒素固溶チタン焼結体の製造方法 | |
WO2018181107A1 (ja) | 焼結アルミニウム合金材およびその製造方法 | |
Vidyasagar et al. | Development of 2024 AA-Yttrium composites by spark plasma sintering | |
Soyama et al. | PM Non Ferrous: TNB-V5 Alloy Modification through Elemental Powder Metallurgy | |
Izadi et al. | The investigation of the microstructure and mechanical properties of ordered alominide-iron (boron) nanostructures produced by mechanical alloying and sintering |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 14877708 Country of ref document: EP Kind code of ref document: A1 |
|
ENP | Entry into the national phase |
Ref document number: 2015556775 Country of ref document: JP Kind code of ref document: A |
|
REEP | Request for entry into the european phase |
Ref document number: 2014877708 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 15110551 Country of ref document: US Ref document number: 2014877708 Country of ref document: EP |
|
NENP | Non-entry into the national phase |
Ref country code: DE |