• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    POWDERED MATERIAL OF SOLID NITROGEN IN TITANIUM SOLUTION, TITANIUM MATERIAL, AND METHOD FOR PRODUCING POWDERED MATERIAL OF SOLID NITROGEN IN TITANIUM SOLUTION. The present invention relates to a method for producing a powder material from a solid nitrogen solution in titanium, characterized in that a titanium powder material consisting of titanium powder particles is heated in an atmosphere which contains nitrogen to form a solid solution of nitrogen atoms in the matrix of titanium powder particles.
    公开号:BR112016016577B1
    申请号:R112016016577-2
    申请日:2014-12-26
    公开日:2021-05-04
    发明作者:Katsuyoshi Kondoh
    申请人:Hi-Lex Corporation；Katsuyoshi Kondoh；
    IPC主号:
    专利说明:

    FIELD OF TECHNIQUE
    [0001] The present invention relates to titanium powder and titanium materials, and more particularly to titanium powder reinforced by a solid nitrogen solution in titanium, titanium materials and methods for the production of such titanium powder reinforced and a titanium material. TECHNICAL BACKGROUND
    [0002] Titanium is a light weight material whose specific gravity is as low as about half that of steel and which is characterized by its high corrosion resistance and high strength. Titanium is therefore used for parts of aircraft, railway vehicles, two-wheeled vehicles, automobiles, etc., for which a reduction in weight is highly desired, household appliances, construction members, etc., titanium is also Used as a material for medical use due to its high corrosion resistance.
    [0003] However, titanium applications are limited due to its high material cost compared to iron and steel materials and aluminum alloys. In particular, titanium alloys have a tensile strength as high as 1,000 MPa or higher, but do not have sufficient ductility (elongation to crack). Furthermore, titanium alloys have an insufficient plastic workability at normal temperature or in a low temperature range. Pure titanium has an elongation to break as high as more than 25% at normal temperature and has excellent plastic workability over a low temperature range. However, pure titanium has a tensile strength as low as about 400 to 600 MPa.
    [0004] Several studies have been carried out in response to a great need for titanium that has both a high strength and a high ductility and to the reduction in cost of titanium material. In particular, various techniques for strengthening titanium using relatively inexpensive elements such as oxygen and nitrogen, rather than expensive elements such as vanadium, scandium and niobium, have been studied in the related art in order to achieve a reduction in cost.
    [0005] For example, the Journal of the Japan Institute of Metals and Materials, Volume 72, No. 12 (2008), pages 949 to 954 (Non-patent Literature 1), entitled "Effect of Nitrogen on Tensile Deformation Behavior and Development of Deformation Structure in Titanium", describes the use of nitrogen as an alloying element for titanium alloys. Specifically, Non-Patent Literature 1 discloses that titanium sponge and TiN powder are weighed in predetermined compositions and are arc cast to produce Ti-N alloys with varying concentrations of nitrogen. In this case, both high strength and high ductility can be achieved if a homogeneous solid solution of nitrogen atoms and a Ti matrix is formed.
    [0006] Another method is a technique of adding TiN particles to molten Ti to form a solid solution of nitrogen atoms in a Ti matrix when the mixture of TiN and molten Ti particles solidifies. Also in this case, both high strength and high ductility can be achieved if a homogeneous solid solution of nitrogen atoms in the Ti matrix is formed. LIST OF QUOTES NON-PATENT LITERATURE
    [0007] NPTL 1: Journal of the Japan Institute of Metals and Materials, Volume 72, No. 12 (2008), pages 949 to 954 SUMMARY OF THE INVENTION TECHNIQUE PROBLEM
    [0008] In conventional fusion methods (in particular, a method of adding TiN particles to molten Ti), nitrogen atoms are significantly diffused and therefore are concentrated on top of the molten Ti. As a result, it is difficult to evenly disperse nitrogen in a large ingot, which significantly reduces ductility.
    [0009] It is an object of the present invention to provide a method for producing titanium powder that contains a solid solubilized nitrogen, in which nitrogen atoms can be uniformly diffused in a matrix of Ti particles to form a solid solution.
    [0010] It is another object of the present invention to provide a titanium powder and a titanium material that have both a high strength and a high ductility by uniformly diffusing nitrogen atoms into a matrix of Ti powder particles to form a solution solid. SOLUTION TO THE PROBLEM
    [0011] A method for producing titanium powder containing a solid solubilized nitrogen, according to the present invention, comprises the step of heating titanium powder comprising titanium particles in an atmosphere containing nitrogen to dissolve the atoms of nitrogen and form a solid solution of the nitrogen atom in a matrix of titanium particles. A heating temperature for the formation of solid solution of the nitrogen atom in the matrix of titanium particles is preferably 400°C or more and 800°C or less.
    [0012] In the titanium powder containing the solid solubilized nitrogen produced by the above method, the titanium particle preferably has a nitrogen content of 0.1% by mass or more and 0.65% by mass or less. By way of reference, the nitrogen contents of four types of pure titanium specified by Japanese Industrial Standards (JIS) are as follows.
    [0013] JIS H 4600 Type 1: 0.03% by mass or less
    [0014] JIS H 4600 Type 2: 0.03% by mass or less
    [0015] JIS H 4600 type 3: 0.05% by mass or less
    [0016] JIS H 4600 of type 4: 0.05% by mass or less
    [0017] A titanium material is a material produced by forming titanium powder that contains solid solubilized nitrogen in a predetermined shape. In one embodiment, the titanium material is a pure Ti powder extruded material, the extruded material has a nitrogen content of 0.1% by mass to 0.65% by mass, and the extruded material has an elongation up to breakage of 10% or more.
    [0018] Examples of a method for compacting titanium powder containing solid solubilized nitrogen to produce titanium material include powder compaction and sintering, hot extrusion, hot rolling, thermal spraying, metal injection molding , powder additive manufacturing, etc.
    [0019] The functions and effects or technical significance of the above characteristics will be described in the following sections. BRIEF DESCRIPTION OF THE DRAWINGS
    [0020] Figure 1 is a diagram schematically showing the features of the present invention.
    [0021] Figure 2 is a diagram showing the data measured with a differential thermogravimetric analyzer.
    [0022] Figure 3 is a diagram showing the diffraction peak shifts of Ti occasioned by heat treatment for the formation of a solid nitrogen solution.
    [0023] Figure 4 shows the measurement result of crystalline orientation analysis (SEM-EBSD).
    [0024] Figure 5 is a diagram showing the relationship between stress and strain.
    [0025] Figure 6 is a diagram showing the relationship between heat treatment time and nitrogen and oxygen contents.
    [0026] Figure 7 is a diagram showing the relationship between nitrogen content and Vickers Hv microhardness.
    [0027] Figure 8 is a diagram showing the relationship between the proportion of the flow rate of oxygen gas and the contents of nitrogen and oxygen. DESCRIPTION OF MODALITIES
    [0028] Figure 1 is a diagram schematically showing the features of the present invention. First, the profile of the present invention will be described with reference to Figure 1, and more detailed data, etc. will then be described. TITANIUM POWDER PREPARATION
    [0029] A titanium powder produced from a multiplicity of titanium particles is prepared. As used herein, the "titanium particles" can be either pure titanium particles or titanium alloy particles. THERMAL TREATMENT FOR THE FORMATION OF SOLID SOLUTION
    [0030] Titanium powder comprising titanium particles is heated in an atmosphere containing nitrogen and retained therein to uniformly diffuse the nitrogen atoms in a matrix of the titanium particles to form a solid solution, so that a solid solution nitrogen in the titanium powder is eventually produced.
    [0031] For example, the heating conditions are as follows. Heating atmosphere: 100% by volume N2 gas Gas flow rate: 5 l/min Heating temperature: 400 to 600°C Retention time: 1 to 2 hours
    [0032] Through the above heat treatment to form solid solution, nitrogen atoms are evenly diffused into the matrix of the titanium powder particles to form a solid solution. Either a tubular (non-rotating) heating furnace or a rotating furnace furnace can be used as a sintering phenomenon between the titanium particles does not occur in the above heating method.
    [0033] For example, titanium powder containing the solid solubilized nitrogen produced in this way is compacted by powder compaction and sintering, hot extrusion, hot rolling, thermal spraying, metal injection molding, powder additive manufacturing , etc. RESEARCH WITH DIFFERENTIAL THERMOGRAVIMETRIC ANALYZER (TG-DTA)
    [0034] The pure Ti raw material powder was put into a furnace. With nitrogen gas being introduced into the furnace at a flow rate of 150 ml/min, the pure Ti raw material powder was heated from normal temperature to 800°C (1,073 K). The weight began to increase at a temperature close to 400°C (673 K), and the weight subsequently increased significantly with an increase in temperature. The result is shown in Figure 2. In Figure 2, TG (thermogravimetry) represents a change in weight and DTA (differential thermal analysis) represents an exothermic/endothermic behavior. MEASUREMENT OF NITROGEN AND OXYGEN CONTENT
    [0035] With nitrogen gas being introduced into a tubular heating furnace at a flow rate of 5 l/min, the pure Ti powder was heated to 400°C (673 K), 500°C (773 K) and 600°C (873 K) for one hour. After that, the nitrogen content and the oxygen content in the resulting Ti powder were measured. The result is shown in Table 1. TABLE 1

    [0036] Table 1 shows that the nitrogen content increased with an increase in the heating temperature. However, the oxygen content changed very little. This shows that the oxidation of Ti powder in the heating method was restricted.
    [0037] The result in Table 1 is well compatible with the result obtained by the differential thermogravimetric analyzer (TG-DTA). It is therefore desirable for the heating temperature to be 400°C (673 K) or more in order to form a solid solution of nitrogen atoms in a Ti matrix. However, heating temperatures higher than 800°C they cause partial sintering between the Ti particles. It is therefore desirable for the heating temperature to be 800°C or less. RESEARCH WITH DIFFRACTION PEAKS
    [0038] Figure 3 shows diffraction peak shifts of Ti caused by heat treatment for the formation of a solid nitrogen solution. Specifically, with nitrogen gas being introduced into a tubular heating furnace at a flow rate of 5 L/min, the pure Ti powder was heated at 600°C (873 K) for one hour and two hours. Thereafter, X-ray diffraction (XRD) analysis of the resulting Ti powder was conducted.
    [0039] As can be seen from Figure 3, the diffraction peaks of Ti are shifted to lower angles if the pure titanium raw material powder is subjected to heat treatment to form a solid nitrogen solution. These peak shifts show that a solid solution of nitrogen atoms in a Ti matrix has been formed.
    [0040] The oxygen and nitrogen contents in the above specimens were measured. The result is shown in Table 2. TABLE 2

    [0041] The result of Table 2 shows that the oxygen content was very little changed, and the nitrogen content increased with an increase in the heating time. RESEARCH WITH CRYSTALLINE ORIENTATION ANALYSIS (WITHOUT-EBSD)
    [0042] Each of the Ti powders was formed and compacted through pulsed plasma sintering. The resulting sintered body was hot extruded to produce an extruded material having a diameter Φ of 7 mm.
    [0043] In pulsed plasma sintering, each Ti powder was heated in a vacuum atmosphere at 800°C for 30 minutes, and a pressure of 30 MPa was applied to each Ti powder in the heating method.
    [0044] In hot extrusion, the sintered body was heated in an argon gas atmosphere at 100°C for 5 minutes. The heated sintered body was immediately extruded at an extrusion rate of 37 to produce an extruded material having a diameter Φ of 7 mm.
    [0045] The result of measuring grain size by crystalline orientation analysis (SEM-EBSD) shows that the grain size decreased with an increase in nitrogen content, that is, the crystal grains became smaller according to the nitrogen content. nitrogen was increased. The result is shown in Figure 4. This occurs because a part of the nitrogen atoms that form a solid solution was diffused and concentrated in Ti grain boundaries and the thickening of the crystal grains was restricted by the drag effect of the solute. . RESISTANCE MEASUREMENT
    [0046] Strength was measured for extruded materials produced from the following Ti powders. "Ti powder heated for one hour", ie Ti powder subjected to heat treatment to form a solid nitrogen solution for one hour and which has a nitrogen content of 0.290% by mass, is called "powder of Ti heated for two hours", that is, the Ti powder subjected to heat treatment to form a solid nitrogen solution for two hours and which has a nitrogen content of 0.479% by mass, and the "matter powder - Ti cousin" (nitrogen content: 0.018% by mass) that was not subjected to heat treatment to form a solid nitrogen solution. The result is shown in Figure 5 and Table 3. TABLE 3

    [0047] As can be seen from Figure 5 and Table 3, Ti powders subjected to heat treatment for the formation of a solid nitrogen solution exhibited an increased strength due to the formation of a solid solution of nitrogen atoms. Ti powders subjected to heat treatment to form a solid nitrogen solution also exhibited reduced elongation, however, the elongations of both Ti powders are higher than 10%. These Ti powders therefore have a high ductility as a Ti material.
    [0048] An extruded material produced from "Ti powder heated for 3 h" (nitrogen content: 0.668% by mass, oxygen content: 0.265% by mass), ie Ti powder subjected to heat treatment for the formation of a solid nitrogen solution for 3 hours, it exhibited an increased tensile strength (UTS) of 1,264 MPa and a 0.2% increase in the yield strength (YS) of 1,204 MPa, but exhibited a significantly reduced elongation of 1.2%. A preferred upper limit for the nitrogen content is therefore 0.65% by mass. A lower limit of nitrogen content is 0.1% by mass in view of the improvement in strength. RELATIONSHIP BETWEEN THERMAL TREATMENT TIME AND NITROGEN AND OXYGEN CONTENT
    [0049] Pure Ti powder (mean grain size: 28 µm, purity: > 95%) was used as a starting material. With nitrogen gas (gas flow rate: 3 l/min) being introduced into a tube furnace, the Ti raw material powder was placed in the tube furnace, and heat treatment to form a solid nitrogen solution was carried out at 600°C for 10 to 180 minutes. The relationship between heat treatment time and nitrogen and oxygen contents in each of the resulting Ti powders was measured. The result is shown in Figure 6 and Table 4. TABLE 4

    [0050] As can be seen from Figure 6 and Table 4, the nitrogen content increases substantially linearly with the time of heat treatment. This shows that the nitrogen content in Ti powder can be controlled by the heat treatment time. On the other hand, the oxygen content does not increase with heat treatment time and is substantially constant. This shows that oxidation did not occur in the heat treatment method. Ti powder that has a targeted nitrogen content can therefore be produced by this method of production. RELATIONSHIP BETWEEN NITROGEN CONTENT AND MICRODURATION OF VICKERS HV
    [0051] The Nitrogen-containing Ti powders shown in Table 4 were heated and pressed with a pulsed plasma sintering system (SPS) to produce the sintered bodies (diameter: 40 mm, thickness: 10 mm).
    [0052] Pulsed plasma sintering was performed under the following conditions. Temperature: 1000°C Pressing force: 30 MPa Sintering time: 30 minutes Degree of vacuum: 6 Pa
    [0053] The Vickers microhardness (load: 50 g) of these sintered bodies was measured. The result is shown in Figure 7 and Table 5. TABLE 5

    [0054] As can be seen from Figure 7 and Table 5, the Vickers hardness increased substantially linearly with an increase in the nitrogen content in the Ti powder. This shows that the hardness of the sintered body was significantly increased by formation of a solid solution of nitrogen atoms in the Ti powder. RELATIONSHIP BETWEEN THE OXYGEN GAS FLOW RATE PROPORTION AND THE OXYGEN AND NITROGEN CONTENT
    [0055] Pure Ti powder (mean grain size: 28 µm, purity: > 95%) was used as a starting material. With nitrogen gas and oxygen gas being introduced at various mixing rates into a tube furnace, the Ti feedstock powder was placed in the tube furnace and heated to 600°C for 60 minutes. The nitrogen content and oxygen content in each of the resulting Ti powders were measured. The result is shown in Figure 8 and Table 6. TABLE 6

    [0056] As can be seen from Figure 8 and Table 6, when the proportion of oxygen gas is 10% by volume or less, the oxygen content does not increase significantly, which shows that only nitrogen atoms are diffused in a Ti matrix to form a solid solution. However, when the proportion of oxygen gas is higher than 15% by volume, the oxygen content also increases, which shows that both nitrogen atoms and oxygen atoms can be diffused into a Ti matrix to form a solid solution. According to this method of production, Ti powder in which not only nitrogen atoms but also oxygen atoms are diffused to form a solid solution can be produced by adjusting the mixing ratio of oxygen and gas. nitrogen in a heat treatment atmosphere. INDUSTRIAL APPLICABILITY
    [0057] The present invention can be advantageously used to produce titanium powder reinforced by a solid solution of nitrogen in titanium and which maintains adequate ductility by uniformly diffusing the nitrogen in a matrix to form a solid solution, and a titanium material.
    权利要求:
    Claims (2)
    [0001]
    1. Method for producing titanium powder containing a solid solubilized nitrogen, characterized in that it consists of the step of: heating titanium powder consisting of titanium particles in a nitrogen containing atmosphere to dissolve nitrogen atoms and forming a solid solution of nitrogen atoms in a matrix of the titanium particles, wherein a heating temperature to form the solid solution of nitrogen atoms in the matrix of titanium particles is 400 °C or more and 600 °C or less , and heating causes the titanium particles to have a nitrogen content of 0.1% by mass or more and 0.65% by mass or less.
    [0002]
    2. Method for the production of titanium powder containing solid solubilized nitrogen, according to claim 1, characterized in that the heating of the titanium powder in the nitrogen-containing atmosphere occurs for a period of time corresponding to the temperature of heating to cause the titanium particles in the titanium particle matrix to have a nitrogen content equal to or greater than 0.1% by mass and 0.65% by mass or less.
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    引用文献:
    公开号 | 申请日 | 公开日 | 申请人 | 专利标题
    JPS61110734A|1984-11-02|1986-05-29|Shinroku Saito|Manufacture of titanium composite material|
    JPS6360296A|1986-08-30|1988-03-16|Nippon Steel Corp|Production of surface-treated steel sheet having excellent rustproofing property|
    JPH0343338B2|1986-09-01|1991-07-02|Nippon Steel Corp|
    JP3006120B2|1990-05-18|2000-02-07|トヨタ自動車株式会社|Ti-Al alloy and method for producing the same|
    DE69730133T2|1996-03-26|2004-12-09|Citizen Watch Co., Ltd., Nishitokyo|TITANIUM OR TITANIUM ALLOY AND SURFACE TREATMENT METHOD THEREFOR|
    JP4408184B2|2001-03-26|2010-02-03|株式会社豊田中央研究所|Titanium alloy and manufacturing method thereof|
    JP5172465B2|2008-05-20|2013-03-27|三菱電機株式会社|Discharge surface treatment electrode manufacturing method and discharge surface treatment electrode|
    CN101602108B|2009-07-10|2012-01-04|西北工业大学|Method for preparing titanium-base hard material powder|
    US8158964B2|2009-07-13|2012-04-17|Seagate Technology Llc|Schottky diode switch and memory units containing the same|
    JP5808894B2|2010-08-20|2015-11-10|日本発條株式会社|High strength titanium alloy member and manufacturing method thereof|
    JP5758204B2|2011-06-07|2015-08-05|日本発條株式会社|Titanium alloy member and manufacturing method thereof|
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    JP2015160970A|2014-02-26|2015-09-07|学校法人立命館|Metallic material and method for producing the same|
    KR20170019366A|2014-05-16|2017-02-21|디버전트 테크놀로지스, 인크.|Modular formed nodes for vehicle chassis and their methods of use|
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    法律状态:
    2019-07-30| B06U| Preliminary requirement: requests with searches performed by other patent offices: procedure suspended [chapter 6.21 patent gazette]|
    2020-10-06| B07A| Application suspended after technical examination (opinion) [chapter 7.1 patent gazette]|
    2021-03-09| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|
    2021-05-04| B16A| Patent or certificate of addition of invention granted [chapter 16.1 patent gazette]|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 26/12/2014, OBSERVADAS AS CONDICOES LEGAIS. |
    优先权:
    申请号 | 申请日 | 专利标题
    JP2014011362|2014-01-24|
    JP2014-011362|2014-01-24|
    PCT/JP2014/084530|WO2015111361A1|2014-01-24|2014-12-26|Powder material of solid solution of nitrogen in titanium, titanium material, and process for producing powder material of solid solution of nitrogen in titanium|
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