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US20130071283A1 - Titanium alloy complex powder containing ceramic and process for production thereof, consolidated titanium alloy material using this powder and process for production thereof - Google Patents

Titanium alloy complex powder containing ceramic and process for production thereof, consolidated titanium alloy material using this powder and process for production thereof Download PDF

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US20130071283A1
US20130071283A1 US13/701,182 US201113701182A US2013071283A1 US 20130071283 A1 US20130071283 A1 US 20130071283A1 US 201113701182 A US201113701182 A US 201113701182A US 2013071283 A1 US2013071283 A1 US 2013071283A1
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titanium alloy
powder
hydrogenated
added
titanium
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Osamu Kano
Hideo Takatori
Satoshi Sugawara
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Toho Titanium Co Ltd
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Toho Titanium Co Ltd
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Assigned to TOHO TITANIUM CO., LTD. reassignment TOHO TITANIUM CO., LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: KANO, OSAMU, SUGAWARA, SATOSHI, TAKATORI, HIDEO
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    • B22F1/0003—
    • 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
    • B22F8/00—Manufacture of articles from scrap or waste metal 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
    • B22F1/12—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
    • 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
    • B22F3/14—Both compacting and sintering simultaneously
    • B22F3/15—Hot isostatic pressing
    • 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
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/023—Hydrogen absorption
    • 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
    • C22C1/05—Mixtures of metal powder with non-metallic powder
    • 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
    • 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
    • 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
    • Y02P10/20—Recycling
    • 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
    • Y02W—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO WASTEWATER TREATMENT OR WASTE MANAGEMENT
    • Y02W30/00—Technologies for solid waste management
    • Y02W30/50—Reuse, recycling or recovery technologies

Definitions

  • the present invention relates to titanium alloy complex powder and a process for production thereof, titanium alloy material using this powder, and a process for production thereof, and in particular, relates to titanium alloy material and a process for production thereof using titanium alloy scrap or titanium alloy ingot as a raw material.
  • Titanium alloy in particular, Ti-6Al-4V alloy has been well known as a material for airplanes.
  • the titanium alloy is produced by a vacuum arc remelting method in which after adding Al—V alloy at an appropriate amount, this is pressed into briquettes, the briquettes are mutually bonded to form an electrode for remelting, the electrode for remelting is set in the vacuum arc remelting furnace, and the electrode is remelted in the vacuum to produce alloy ingots.
  • it can be also produced by an electron beam remelting method in which materials for remelting consisting of titanium material and Al—V master alloy are supplied to a hearth, an electron beam is irradiated on the material to remelt them, and the melted metal is poured into a mold arranged downstream of the hearth to produce alloy ingots.
  • a powder method can realize a condition in which fine particles are uniformly dispersed after sintered product, as long as raw material powder and fine particles are uniformly mixed.
  • the titanium alloy powder has inferior workability and formability compared to pure titanium powder, as a result, there is another problem that sintering density is difficult to be increased.
  • Ti-6Al-4V alloy has small plastic deformability, it is known that sintering density is difficult be increased by an ordinary method by the powder method (See Reference 1 below).
  • the Blended Elemental Powder Metallurgy Process (hereinafter simply referred to as “BE Process”) in which pure titanium powder and Al-40% V alloy powder are used as raw materials instead of using titanium alloy powder, is employed.
  • a dense titanium alloy material has been ordinarily produced by vacuum sintering of solid component consisting of formed powder and by subsequent HIP (Hot Isostatic Press) process.
  • HIP Het Isostatic Press
  • An object of the present invention is to provide titanium alloy complex powder having superior quality by the powder method using titanium alloy scrap or titanium alloy ingot as a raw material, and is to provide titanium alloy material and a process for production thereof.
  • titanium alloy complex powder having uniform composition can be produced in low cost, by using the titanium alloy scrap or titanium alloy ingot as a raw material, hydrogenating it to generate hydrogenated titanium alloy, grinding and sifting the hydrogenated titanium alloy to obtain hydrogenated titanium alloy powder, adding a third component to this, and dehydrogenating it to generate titanium alloy powder; or by using the titanium alloy scrap or titanium alloy ingot as a raw material, hydrogenating it to generate hydrogenated titanium alloy, grinding and sifting the hydrogenated titanium alloy to obtain hydrogenated titanium alloy powder, dehydrogenating it to generate titanium alloy powder, and further adding a third component, and thus the present invention has been completed.
  • titanium alloy complex powder of the present invention has ceramic powder, and furthermore, the ceramic powder is at least one selected from a group consisting of SiC, TiC, SiO x , TiO x , and Al 2 O 3 .
  • index x is a real number which is in 1 ⁇ x ⁇ 2.
  • each ceramic added to the titanium alloy powder is in a range from 0.01 to 0.15 wt %, and the total added amount is in a range from 0.01 to 0.3 wt % in the case in which two or more ceramic powders are added.
  • particle size of the titanium alloy powder be not more than 150 ⁇ m.
  • the titanium alloy powder raw material contain aluminum and vanadium, or contains at least one kind selected from zirconium, tin, molybdenum, iron and chromium in addition to aluminum and vanadium.
  • a process for production of titanium alloy powder of the present invention has steps of hydrogenating titanium alloy raw material to generate hydrogenated titanium alloy as a raw material, grinding the hydrogenated titanium alloy as an intermediate material to obtain hydrogenated titanium alloy powder, and as a final step, adding ceramic powder and then dehydrogenating them; or dehydrogenating the hydrogenated titanium alloy powder and then adding and mixing ceramic powder.
  • the above noted titanium alloy complex powder be treated by CIP (Cold Isostatic Press) process and subsequent HIP process, or by HIP process after filling the above noted titanium alloy complex powder into a capsule.
  • Titanium alloy material of the present invention is produced by the above noted process.
  • ratio of density of the titanium alloy material produced by the above process against the true density be not less than 99%.
  • titanium alloy material of the present invention is produced not via remelting and solidifying, by treating by CIP process and subsequent HIP process, or by treating by HIP process after encapsulating into capsule, distribution of ceramic component can be maintained in uniform and fine condition as originally is added, as a result, titanium alloy material in which ceramic particles are uniformly and finely distributed can be produced, and titanium alloy material having high strength and toughness can be provided in low cost.
  • FIG. 1 is a flow chart diagram showing desirable process for production of titanium alloy powder and titanium alloy material of the present invention (ceramic is added before dehydrogenation).
  • FIG. 2 is a flow chart diagram showing desirable process for production of titanium alloy powder and titanium alloy material of the present invention (ceramic is added after dehydrogenation).
  • the titanium alloy complex powder of the present invention is characterized in that ceramic powder is added. It is desirable that the ceramic powder of the present invention be at least one selected from a group consisting of SiC, TiC, SiO x , TiO x , and Al 2 O 3 .
  • index x is a real number which is in 1 ⁇ x ⁇ 2. It means SiO in the case in which x is 1 and SiO 2 in the case in which x is 2. TiO x is determined similarly.
  • This ceramic powder(s) is/are added to titanium alloy powder at an appropriate amount to obtain titanium alloy complex powder.
  • the ceramic powder is dispersed uniformly in titanium alloy, and as a result, a dispersion-strengthened titanium sintering alloy can be obtained.
  • whisker state SiC and TiC can also be used.
  • whisker state SiC and TiC By adding whisker state SiC and TiC to titanium powder, strength of titanium alloy sintered and produced can be greatly improved. It is desirable that the above noted whisker state SiC and TiC having aspect ratio in a range from 5 to 50 be used.
  • SiC and TiC can newly generate TiSi 2 and TiC by reacting with titanium alloy.
  • TiSi 2 can improve toughness of titanium alloy. Furthermore, TiC which is generated during forming process has good consistency with titanium alloy matrix. Therefore, conventionally not known effect in which higher strength can be exhibited compared to a case in which TiC is extrinsically added as an alloy element, can be obtained.
  • an alloy scrap or alloy ingot such as titanium alloy chips, titanium alloy forged chips, edge material of titanium alloy rod or the like can be used.
  • length or dimension of these titanium alloy raw material be controlled in predetermined size beforehand. For example, it is desirable to cut at not more than 100 mm beforehand in the case of alloy chips. By cutting at the above-mentioned length, subsequent hydrogenating process can be efficiently promoted. In addition, in the case of block shaped alloy scrap such as the forged chips, there is no difficulty as long as it has a size which can be put into hydrogenating furnace. In the case in which the alloy raw material is titanium alloy ingot, it is desirable to treat so as to be cut chips having predetermined size by a cutting process.
  • the titanium alloy raw material treated and controlled as mentioned above is brought into the hydrogenating process under hydrogen atmosphere.
  • the hydrogenating process is desirably performed at a temperature range from 500 to 650° C. Since hydrogenating process reaction of alloy raw material is exothermic reaction, any heating operation by a heating furnace is not necessary accompanied by promotion of hydrogenating reaction, thus hydrogenating reaction can be promoted automatically.
  • the alloy as an intermediate material which is hydrogenation treated (hereinafter simply referred to as “hydrogenated titanium alloy”) is then cooled to room temperature, and is desirably ground and sifted until hydrogenated titanium powder has predetermined particle size under inert atmosphere such as argon gas or the like. Subsequently, it is desirable to add the ceramic powder of the present invention.
  • hydrogenated titanium alloy powder in which ceramic powder is added is desirably treated by dehydrogenation process.
  • dehydrogenation process By heating until it reaches a high temperature range in an atmosphere maintained at reduced pressure, dehydrogenation can be effectively promoted.
  • the temperature of dehydrogenating process is desirably performed in a range from 500 to 800° C. Since dehydrogenation reaction is endothermic reaction, in contrast to the above-mentioned hydrogenation process reaction, heating operation is necessary until hydrogen is completely generated from hydrogenated titanium alloy powder.
  • Titanium alloy powder obtained by the above-mentioned dehydrogenating process is sometimes sintered together, in this case, it is desirable that the grinding and sifting processes be performed again.
  • Hydrogenated titanium alloy powder which is ground and sifted until it has predetermined particle size, can be dehydrogenated as it is. It is desirable that ceramic powder of the present invention be added and mixed with titanium alloy powder of which dehydrogenation process is completed. In this case, an ordinary mixing means such as V-type mixing machine or the like can be employed to add and mix.
  • ceramic powder can be added before or after dehydrogenation process. Aggregation and sintering of titanium alloy powder during dehydrogenation can be prevented and oxygen content in titanium alloy powder can be maintained in low level in the case in which ceramic powder is added before dehydrogenation process. However, load during steps is increased, that is, dehydrogenation furnace and devices for grinding and sifting after dehydrogenation process should be controlled depending on kind of ceramic.
  • Dehydrogenation process can be promoted more efficiently in the case in which dehydrogenation process is performed before adding ceramic powder. Furthermore, dehydrogenation furnace and devices for grinding and sifting are easily controlled.
  • particle size of the hydrogenated titanium alloy powder after grinding and sifting be controlled in a range from 10 to 150 ⁇ m. By controlling in the range, consolidating can be promoted in subsequent consolidating process.
  • ceramic powder used in the present invention be at least one selected from a group of particles of SiC, SiO x , TiO x , TiC and Al 2 O 3 .
  • Particle size of the ceramic powder is desirably in a range from 0.01 to 50 ⁇ m, more desirably in a range from 0.1 to 20 ⁇ m.
  • particles of the third component may be undesirably aggregated each other during mixing with titanium alloy powder.
  • dispersibility is undesirably not sufficient.
  • ratio of adding of the ceramic powder be 0.01 to 0.15 wt % in the case in which one kind of SiC, SiO x , TiO x , TiC and Al 2 O 3 is added.
  • the total ratio of adding be 0.01 to 0.3 wt % of in the case in which two kinds or more of these ceramic powders are added.
  • the consolidating process be performed by combining CIP and HIP appropriately.
  • titanium alloy complex powder obtained in the above-mentioned method be filled in a CIP rubber, treated at 100 to 200 MPa, then filled in a HIP capsule, and HIP treated at a temperature not higher than ⁇ transformation point at 50 to 200 MPa for 1 to 5 hours. After such CIP process and subsequent HIP process, consolidated titanium alloy material can be obtained.
  • titanium alloy complex powder obtained in the above-mentioned method be filled in a HIP capsule and HIP treated at a temperature not higher than ⁇ transformation point at 50 to 200 MPa for 1 to 5 hours without CIP process.
  • Consolidated titanium alloy material can also be obtained by HIP process alone.
  • SiC added to hydrogenated alloy powder commercially available powdered sample can be used.
  • particle size of SiC added is desirably in a range from 0.01 ⁇ m to 50 ⁇ m, and more desirably in a range from 0.1 ⁇ m to 20 ⁇ m.
  • size and existence frequency of dispersion phase in structure of final product can be desirably controlled without negatively affecting to properties of titanium alloy final product.
  • SiC powder added to titanium alloy complex powder reacts with titanium in the matrix as following reaction formula to generate TiC and Si.
  • TiC generated in the above reaction is uniformly dispersed in the matrix with keeping coherency with the matrix in titanium, as a result, tensile strength is also superior compared to a case in which SiC is not added.
  • SiC silicon carbide
  • SiC silicon carbide
  • Si metal generated in the matrix reacts with titanium in the matrix to generate TiSi 2 .
  • TiSi 2 generated in the matrix is deposited with keeping coherency with the matrix phase, and toughness of titanium alloy material can be increased.
  • TiC titanium alloy powder
  • additional ratio of TiC be controlled in a range from 0.01% to 0.15% of weight of titanium alloy powder.
  • Particle size of TiC added is desirably in a range from 0.01 ⁇ m to 50 ⁇ m, and more desirably in a range from 0.1 ⁇ m to 20 ⁇ m.
  • size and existence frequency of dispersion phase in structure of final product can be desirably controlled without negatively affecting to properties of titanium alloy final product of which titanium alloy powder of the present invention is consolidated.
  • TiC in titanium alloy material after HIP process is maintained in a range from 0.01 to 50 ⁇ m which is a particle size of addition, and its existence frequency is not less than 5 particles/mm 2 .
  • TiC phase uniformly and finely dispersed in the matrix greatly contributes to improve mechanical properties such as tensile strength, fatigue strength or the like by dispersion strengthening.
  • SiO 2 powder added to titanium alloy complex powder reacts with titanium in the matrix as following reaction formula to generate TiO 2 , Si, and TiSi 2 .
  • TiO 2 generated in the above reaction remains in titanium alloy, as a result, dispersion strengthening of titanium alloy itself occurs. Furthermore, TiSi 2 generated in the above reaction contributes to improve toughness of titanium alloy.
  • TiO x such as SiO or the like is used instead of SiO 2 powder
  • TiO x and Si are generated in a similar way to the above reaction, it reacts with Ti to generate TiSi 2 , to contribute to improve toughness of titanium alloy.
  • TiO 2 powder which is an example of TiO x
  • CIP process and subsequent HIP process or by HIP process after encapsulating into a capsule mechanical properties of titanium alloy material can be improved.
  • Ranges of added amount and desirable particle size of TiO 2 powder are as same as in the case of TiC addition.
  • titanium alloy Furthermore, in the case in which TiO x such as TiO or the like is added to titanium alloy, mechanical properties of titanium alloy can be improved similarly.
  • Addition of the ceramic powder of the present invention is not limited in one kind, two or more kinds of powder can be added.
  • raw material of ceramic powder is desirably in a range from 0.01 to 0.3 wt %.
  • Particle size of each ceramic added is desirably in a range from 0.01 to 50 ⁇ m, more desirably in a range from 0.01 to 20 ⁇ m.
  • Titanium alloy complex powder controlled by the above-noted process can be efficiently consolidated by CIP process and subsequent HIP process, or by HIP process after filling titanium alloy complex powder into a capsule.
  • titanium alloy such as Ti-6Al-4V alloy, Ti-3Al-2.5V alloy, Ti-6Al-2Sn-4Zr-6Mo alloy, Ti-6Al-6V-2Sn alloy, Ti-10V-2Fe-3Al alloy (10-2-3), Ti-5Al-4V-0.6Mo-0.4Fe alloy (Timetal 54M), Ti-4.5Al-3V-2Fe-2Mo alloy (SP700), Ti-15V-3Cr-3Al-3Sn alloy (15-3-3-3), Ti-4Al-2.5V-1.5Fe alloy (ATI425), Ti-5Al-5V-5Mo-3Cr alloy (Ti-5553) can be used as the above mentioned raw material of titanium alloy powder.
  • Ti-6Al-4V alloy Ti-3Al-2.5V alloy
  • Ti-6Al-2Sn-4Zr-6Mo alloy Ti-6Al-6V-2Sn alloy
  • Ti-10V-2Fe-3Al alloy 10-2-3
  • Ti-5Al-4V-0.6Mo-0.4Fe alloy Timetal 54M
  • Mechanical properties of titanium alloy material containing copper, chromium or iron and being consolidated by the above-mentioned method can be further controlled by subsequent processing such as rolling, extrusion or drawing and heat process.
  • Scrap cut chips of Ti-6Al-4V alloy were cut into chips having length not greater than 10 mm.
  • the chips were inserted into a container and the container was set in a furnace. After vacuum evacuation inside the furnace, heating was started, hydrogen was induced into the furnace after the temperature inside the furnace reached 300° C., and heating was continued until 650° C. while maintaining the inside of the furnace in a slightly pressurized condition by hydrogen.
  • heater output was set at 0, and the condition was maintained as it was until the reaction was completed.
  • TiO 2 powder was each added at 0%, 0.05 wt %, 0.1 wt %, 0.15 wt % and 0.5 wt % to hydrogenated titanium alloy powder having composition of Ti-6% Al-4% V of Example 1, to prepare five samples and each mixed by a V-type mixing machine.
  • TiO 2 powder used was a powder produced by oxygen combustion method of TiCl 4 , and the average particle size was 0.8 ⁇ m.
  • Each sample of hydrogenated titanium alloy powder to which TiO 2 was added was inserted into a container made of titanium, and dehydrogenation process was performed in a vacuum heating furnace. Starting heating after vacuum evacuation, dehydrogenation reaction of which hydrogen gas was separated occurred at about 300° C. Heating was continued to increase the temperature up to 500° C., and then 600° C., dehydrogenation was promoted. Since dehydrogenation reaction is an endothermic reaction, it is important to maintain temperature inside of the furnace at a constant level to perform dehydrogenation efficiently. When the temperature was maintained at 650° C. for 1 hour, the degree of vacuum was recovered. Since the vacuum degree of 1 ⁇ 10 ⁇ 3 mbar was obtained, heating was stopped, and cooled. Since powder taken out of the furnace was partially aggregated, it was crushed by a crushing machine to obtain titanium alloy particle not greater than 300 ⁇ m.
  • TiO 2 added titanium alloy powder of Example 2 was filled in a CIP rubber, and CIP treated at 150 MPa.
  • the CIP compact was encapsulated in a soft steel capsule and HIP treated to obtain titanium alloy material of the present invention.
  • the conditions of HIP were 900° C., 100 MPa and 1 hr. After HIP process, titanium alloy material was taken out, its apparent density was measured and the ratio to theoretical density (hereinafter simply referred to as “density ratio”) was calculated. The result is shown in Table 1.
  • the density ratio of titanium alloy material is increased from 99.1% to 99.5% in the case in which added amount of TiO 2 is increased from 0.05 wt % to 0.15 wt %.
  • TiO 2 added titanium alloy powder of Example 2 was filled in a soft steel capsule and HIP treated.
  • the conditions of HIP were 900° C., 100 MPa and 1 hr. After HIP process, titanium alloy material was taken out, its density was measured and the density was not less than 99%.
  • the density means the ratio of apparent density against true density.
  • Example 3-2 Tension test of titanium alloy material (TiO 2 added Ti-6Al-4V) produced in Example 3-2 was performed. The result is shown in Table 1. In Table 1, results of measuring the density are also shown. There is no difference in the density ratio, tensile strength and elongation observed, between the case in which TiO 2 added Ti-6Al-4V alloy powder is encapsulated into capsule and HIP treated and the case in which CIP treated and subsequently HIP treated.
  • TiO 2 phase existed dispersing uniformly in the matrix.
  • Size and existence frequency of TiO 2 phase are as shown in Table 2.
  • size of TiO 2 phase means maximal diameter of TiO 2 phase dispersed in the matrix.
  • existence frequency of TiO 2 phase means the number of TiO 2 particles confirmed in a unit area of the matrix.
  • the maximal diameter of TiO 2 phase in the matrix of titanium alloy sintered bodies is increased from 5 ⁇ m to 15 ⁇ m in the case in which added amount of TiO 2 to titanium alloy powder is increased from 0.05 to 0.15%. Furthermore, there is a tendency that the number of TiO 2 particles per a unit area of the matrix is increased from 15 particles/mm 2 to 40 particles/mm 2 .
  • SiO 2 powder having size of 2 ⁇ m was each added at 0.05 wt %, 0.1 wt %, 0.15 wt % and 0.5 wt % to titanium alloy powder, and CIP process and subsequent HIP process were performed in a manner similar to those of Examples 3 and 4, to obtain titanium alloy material of the present invention. Next, measurement of the density ratio and the tension test of titanium alloy material obtained were performed.
  • SiO 2 added titanium alloy powder of Example 6 was filled in a soft steel capsule and HIP treated. Conditions of HIP were 900° C., 100 MPa and 1 hr. After HIP process, titanium alloy material was taken out, its density ratio was measured and tension test was performed.
  • the tensile strength was increased from 1050 to 1100 MPa and the elongation is decreased from 15% to 13% and in the case in which added amount of SiO 2 is increased from 0.05 to 0.15 wt %.
  • the density ratio is increased from 99.2 to 99.5%. There is no difference in the density ratio, the tensile strength and the elongation observed, in the case of Example 6-2 in which SiO 2 added Ti-6Al-4V alloy powder was encapsulated into capsule and HIP treated.
  • Example 1 A sample in which no ceramic powder was added to hydrogenated titanium alloy powder of Example 1 was prepared, CIP process and HIP process were performed in a manner similar to those of Examples 3 and 4, and measurement of the density and tension test were performed. The results are shown in Table 1.
  • the elongation was about 15%; however, the tensile strength was decreased to 900 MPa in the case in which no TiO 2 was added.
  • Example 1 A sample in which TiO 2 was added at 0.5 wt % to hydrogenated titanium alloy powder of Example 1 was prepared, CIP process and HIP process were performed in a manner similar to those of Examples 3 and 4, and measurement of the density and the tensile test were performed. The results are shown in Table 1. The elongation was decreased to 2% in the case in which TiO 2 was added at 0.5 wt %.
  • Example 1 A sample in which no SiO 2 powder was added to hydrogenated titanium alloy powder of Example 1 was prepared, CIP process and HIP process were performed in a manner similar to those of Examples 3 and 4 to obtain titanium alloy material. As a result, the density ratio of titanium alloy material obtained was decreased to 98%.
  • Example 3 A sample in which SiO 2 was added at 0.5 wt % to hydrogenated titanium alloy powder of Example 1 was prepared, CIP process and HIP process were performed in a manner similar to those of Examples 3 and 4, and measurement of the density, measurement of the tensile strength and observation of the crystal structure were performed. As a result, as shown in Table 3, the elongation of titanium alloy material was radically decreased to about 4%.
  • the present invention provides titanium alloy powder and titanium alloy material having superior mechanical properties by powder metallurgical method using titanium alloy scrap or titanium alloy ingot as a raw material, and the present invention provides titanium alloy powder, titanium alloy material and process for production thereof.

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US13/701,182 2010-05-31 2011-05-30 Titanium alloy complex powder containing ceramic and process for production thereof, consolidated titanium alloy material using this powder and process for production thereof Abandoned US20130071283A1 (en)

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PCT/JP2011/062392 WO2011152359A1 (fr) 2010-05-31 2011-05-30 Poudre en un composite d'alliage de titane, contenant une céramique, et son procédé de fabrication, et alliage de titane densifié et son procédé de fabrication l'utilisant

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US20170067137A1 (en) * 2015-09-07 2017-03-09 Seiko Epson Corporation Titanium sintered body and ornament
CN107234242A (zh) * 2016-03-29 2017-10-10 精工爱普生株式会社 钛烧结体、装饰品及耐热部件
WO2017190246A1 (fr) * 2016-05-04 2017-11-09 Lumiant Corporation Composite à matrice en siliciure de titane à renfort de carbure de titane formé in situ
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US10422018B2 (en) 2013-05-17 2019-09-24 G. Rau Gmbh & Co. Kg Method and device for remelting and/or remelt-alloying metallic materials, in particular Nitinol
CN106493363A (zh) * 2015-09-07 2017-03-15 精工爱普生株式会社 钛烧结体以及装饰品
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CN107234242A (zh) * 2016-03-29 2017-10-10 精工爱普生株式会社 钛烧结体、装饰品及耐热部件
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WO2017190246A1 (fr) * 2016-05-04 2017-11-09 Lumiant Corporation Composite à matrice en siliciure de titane à renfort de carbure de titane formé in situ
CN108193064A (zh) * 2017-12-26 2018-06-22 天钛隆（天津）金属材料有限公司 一种低成本工业化生产TiC颗粒增强钛基复合材料的方法
CN115485403A (zh) * 2020-03-16 2022-12-16 犹他大学研究基金会 生产钛合金产品的方法
CN111922349A (zh) * 2020-09-21 2020-11-13 西安斯瑞先进铜合金科技有限公司 一种CuCr合金电工触头专用金属铬粉的制备方法
GB2599237A (en) * 2020-09-24 2022-03-30 Bae Systems Plc Powder hot isostatic pressing cycle
GB2599237B (en) * 2020-09-24 2024-01-10 Bae Systems Plc Powder hot isostatic pressing cycle
US12479025B2 (en) 2020-09-24 2025-11-25 Bae Systems Plc Powder hot isostatic pressing cycle
CN115415513A (zh) * 2022-09-23 2022-12-02 西北工业大学 基于均匀性的钛合金和陶瓷增强相球磨混粉工艺的优化方法

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