WO2007139194A1 - 複合材料とその製造方法、ならびに、それに用いる組成物およびそれを用いた刃物 - Google Patents
複合材料とその製造方法、ならびに、それに用いる組成物およびそれを用いた刃物 Download PDFInfo
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- WO2007139194A1 WO2007139194A1 PCT/JP2007/061118 JP2007061118W WO2007139194A1 WO 2007139194 A1 WO2007139194 A1 WO 2007139194A1 JP 2007061118 W JP2007061118 W JP 2007061118W WO 2007139194 A1 WO2007139194 A1 WO 2007139194A1
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- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only borides
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- 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
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
- B22F2005/002—Tools other than cutting tools
Definitions
- the present invention relates to a titanium-based sintering composition in which NiB hard particles are dispersed in a titanium alloy matrix and a composite sintered material using the same. More specifically, the present invention relates to wear resistance and excellent sinterability. The present invention relates to a titanium-based composite material. Furthermore, the present invention relates to a blade using this wear-resistant titanium-based composite material.
- Titanium alloys have higher specific strength and specific toughness than super-strength steel, high-strength aluminum alloys, and the like, and are therefore used in strength parts such as aircraft and racing cars.
- Ti-based composite material As this Ti-based composite material, a titanium-based composite material in which TiB particles are dispersed in a titanium alloy using powder metallurgy, and a method for producing a powder alloy laminate [Titani Diboride / Titaniium Alloy Metal Matrix Micro-composite and process powder metal uladdmg "(Patent Document 1) has been proposed.
- the resulting alloy composition is said to be excellent in strength, rigidity, and wear resistance.
- TiB particle-dispersed composite materials TiB is not thermodynamically balanced with titanium alloys at high temperatures. In order to achieve this, it is premised that sintering should be performed at a low temperature at which reaction is unlikely to occur and at a high pressure. For this reason, there has been a problem that the manufacturing cost is significantly increased.
- Patent Document 2 a Ti alloy for high-density powder sintering that limits the amount of Fe Mo Al VO, the balance being Ti and inevitable impurities, has been proposed as a method that can increase the density at low cost and with high productivity.
- This method combines Fe, which has a high diffusion rate, with Mo, which has a low diffusion rate, in a Ti alloy so that it can be sintered densely in a short time at low temperatures.
- this method has not yet improved the low rigidity, which is a drawback of Ti alloys.
- a liquid phase mainly composed of temporary Ti Mo-B generated immediately below the sintering temperature is used as a sintering promotion phase, and this sintering promotion phase has B as its constituent element and is sintered.
- TiB can be the only effective TiB as reinforcing particles in the Ti alloy, and a technology to improve the strength, rigidity and wear resistance of the resulting sintered Ti alloy material has been proposed (patented) Reference 3).
- Patent Document 1 U.S. Pat.No. 4,968,348
- Patent Document 2 JP-A-5-171321
- Patent Literature 3 Hei 11 1 92843
- the present invention is a composite material comprising a Ti alloy matrix containing Ti as a main component and TiB and NiB dispersed in the Ti alloy matrix.
- the present invention is a blade using a composite material for a blade portion.
- the present invention provides a method for producing a composite material, characterized in that sintering is performed using a mixed powder containing Ti powder and / or Ti alloy powder containing Ti as a main component and NiB powder. It is.
- the present invention provides a composition for sintering that can be used as a sintering promoting phase instead of MoB, and the gist thereof is that titanium powder and / or titanium is a main component. It is a mixed powder comprising the titanium alloy powder and NiB powder.
- the sintering density can be improved as compared with the case where MoB is used as the sintering promoting phase, and the base material (matrix) force is the ⁇ phase mainly composed of titanium.
- a wear-resistant titanium-based composite material in which TiB and NiB are dispersed in at least one titanium alloy is obtained. That power S.
- FIG. 1 shows a structure diagram before sintering of a composite material according to the present invention.
- FIG. 2 shows a structure diagram after sintering of the composite material according to the present invention.
- FIG. 3 is an enlarged view of NiB shown in FIG.
- FIG. 4 is an enlarged view of TiNi, NiB and TiB shown in FIG.
- FIG.5 Shows the state diagram of Ti and B.
- FIG. 6 Shows the phase diagram of Ti and Ni.
- FIG. 7 is a graph showing the wear resistance of the composite material according to the present invention.
- Fig. 1 shows a structure diagram before sintering of the composite material according to the present invention
- Fig. 2 shows a structure diagram after sintering.
- Part of the dispersed Ni in the composite material after sintering is the phase of intermetallic compound TiNi (4 in the figure), TiB (3 in the figure) and Ti ⁇ or ⁇ phase (2 in the figure). ) Exist independently. The remaining Ni exists in the NiB phase (1 in the figure).
- Figure 3 is an enlarged view of NiB, TiB and TiNi (NiTi) present in the Ti alloy matrix before sintering.
- Compound Ni B decomposes at least partially into Ni atoms and B atoms during heating during sintering (eg, 1200 ° C or higher).
- Ni and B atoms diffuse through the Ti alloy matrix, respectively.
- Ni atoms combine with Ti atoms in the Ti alloy matrix to form the intermetallic compound TiNi.
- B atoms combine with Ti atoms in the Ti alloy matrix to form compound TiB.
- NiB is formed. Therefore, a composite material having TiB, NiB, and TiNi shown in FIGS. 2 and 4 can be obtained by sintering. From the distribution of B and Ni in Fig. 2, the overlapping part of B and Ni is the NiB phase, and the part where only B is the TiB phase, confirming the existence of TiB and NiB described above. Therefore, there are TiNi phase, TiB phase, Ti phase, and NiB phase.
- Ti and Ni which are the main components, have a smaller specific gravity difference than Ti and Mo. It became possible to lead to density improvement.
- the presence of the NiB phase is considered to be due to the strong connection between the TiNi phase and the TiB phase due to the NiB phase in the region where the TiNi phase and the TiB phase overlap. .
- the halide contained in the composite material has a detection limit (5ppm) or less by fluorescent X-ray analysis, and becomes a titanium-based composite material having excellent wear resistance.
- the sintered Ti alloy material of the present invention is a sintered Ti alloy material having a matrix mainly composed of a Ti alloy and TiB and NiB dispersed and held in the matrix, the TiNi phase, Ti
- the sintered Ti alloy material of the present invention exhibits excellent strength, rigidity, wear resistance, and fatigue characteristics.
- the sintered Ti alloy of the present invention has a high strength, rigidity, wear resistance and heat resistance.
- NiB solid solution can coexist and high density sintered Ti alloy material can be obtained.
- the densification mechanism by which a high-density sintered Ti alloy can be obtained is not yet clear, but the added NiB decomposes into parts Ni and B, and part of the dispersed Ni is
- the Ti phase of TiNi dissolved in Ti exists independently of the Ti phase of TiB and Ti, and other Ni may exist in the NiB phase.
- Ti B and Ni-B have a high affinity for j3 Ti alloys.
- Ti-B has the strongest attractive force.
- Ti-Ni is repulsive. This is
- This locally generated liquid phase gradually disappears with the diffusion of Ni accompanying sintering, and the brittle soot phase and outflow holes, which are a concern in normal liquid phase sintering, are not generated. That is, in the case of Ti-Ni_B system Ti alloy material, this temporary liquid phase has an action of promoting densification.
- the present invention has been made on the basis of such knowledge and utilizes the interaction between Ti, Ni, and B. That is, according to the present invention, a temporary liquid phase of Ti Ni—B produced immediately below the sintering temperature is densified as a sintering promoting phase by the interaction of Ti, Ni, and B. Conclusion Ti alloy material.
- the content of NiB constituting the sintered Ti alloy material of the present invention is 0.6 to 4.8 wt% (hereinafter, unless otherwise specified, wt%) in the state before sintering (molded body). Means.) If the Ni B content is less than 0.6%, the liquid phase necessary for densification is not supplied near the grain boundary, and if the NiB content exceeds 4.8%, a large amount of TiB particles are precipitated and densified. Is insufficient, and the toughness decreases. Since this NiB partially decomposes during sintering as described above to form TiB, the NiB content of the composite material (the state after sintering) is preferably 0.3 to 2.4. %.
- C1 needs to be controlled to be low in order to smoothly perform these reactions, and the C1 content in a preferable composite material is 0.03% or less.
- the strong reduction reaction of metal sodium can be used to remove chlorine (dehalogenation) and render it harmless.
- the target substance is dried to near dryness, it is mixed with a small amount of sodium while being pulverized in a reducing gas (nitrogen gas) atmosphere using a ball mill or the like to obtain stable sodium chloride.
- reducing gas nitrogen gas
- the sintered Ti alloy material of the present invention may further contain A1.
- A1 is an element that strengthens the a-Ti phase by solid solution and has high effect on Young's modulus as well as strength. Furthermore, the addition of A1 has the effect of suppressing the formation of ⁇ phase, which causes brittle defects in the / 3 Ti alloy.
- Sintered Ti alloy materials containing A1 are both excellent in strength and toughness.
- a preferable content of A1 is 0.1% to 6.0% when the sintered Ti alloy material is 100% by weight. If the A1 content is less than 0.1%, the effect of improving the strength cannot be obtained, and if the A1 content exceeds 6.0%, TiAl precipitates and the toughness decreases. Therefore, the composition range of A1 is preferably 0.1% to 6.0%.
- the Ti alloy matrix of the sintered Ti alloy material (composite material) according to the present invention can be either a Ti Ti alloy or a j3 Ti alloy. As described above, A1 addition can be applied to either a Ti Ti alloy or a / 3 Ti alloy. Is also useful.
- the sintered Ti alloy material containing A1 is preferably one containing Fe, Co or Cu. Specifically, when the sintered Ti alloy material is 100% by weight, at least 0.6 to 4.8% NiB, 1.0 to 7.0% Fe, 1.0 to 8.5% Co, 1.0 to 8.0% 1% or more of Cu, and 0.:! To 6.0% A1 and Ti is 50% or more, the balance is inevitable, and power The alloy material which becomes can be mentioned.
- the sintered Ti alloy material of the present invention may further contain V, Sn, Zr, Nb, and Mn.
- Sn is a neutral element (neutral element).
- ct Ti phase is a solid solution strengthening element that improves tensile strength and fatigue strength and has a high Young's modulus improvement effect.
- Zr is a neutral solid element of the total solid solution type. Like Sn, it is an element that strengthens solid solution and improves Young's modulus as well as strength.
- V, Nb, and Mn are Ti phase stabilizing elements. In particular, it has the effect of suppressing the formation of TiAl, which causes toughness deterioration, and therefore has the effect of containing more A1. In addition to improving heat treatment characteristics, it also has the effect of improving hot and warm workability.
- the content of V is preferably 0.:! To 4.0% when the sintered Ti alloy material is 100% by weight. If the amount of V is less than 0.1%, the strengthening action and j3 stabilizing action are insufficient, and if it exceeds 4.0%, the ⁇ stabilizing action is too strong and the toughness is reduced.
- the Nb content is 1.0 to 4.0 when the sintered Ti alloy material is 100% by weight. / o is preferred.
- Nb has the effect of improving strength properties at high temperatures by coexisting with Ni. . If the amount of Nb is less than 1%, the effect is insufficient, and if it exceeds 4.0%, the stabilizing action is too strong and the toughness is reduced.
- the Sn content is preferably 1.0 to 5.0% when the sintered Ti alloy material is 100% by weight. If the Sn content is less than 1%, the strengthening action and / 3 stabilizing action are insufficient, and if it exceeds 5.0%, the density increases and TiAl precipitates, resulting in a decrease in toughness.
- the content of Zr is preferably 1.5 to 6.0% when the sintered Ti alloy material is 100% by weight. If the amount of Zr is less than 1.5%, the effect is insufficient. If it exceeds 6.0%, a large amount of fine intermetallic compounds with Ti and Si are precipitated, resulting in a decrease in toughness.
- the content of Mn is preferably 1.0 to 6.0% when the sintered Ti alloy material is 100% by weight. If the amount of Mn is less than 1%, the strengthening action and j3 stabilizing action are insufficient, and if it exceeds 6.0%, the stabilizing action is too strong and the toughness is reduced.
- V, Sn, Zr, Nb, and Mn are contained.
- the sintered Ti alloy material at least 0.6 to 4 when the sintered Ti alloy material is 100% by weight. 8% NiB (state before sintering), 1.0 ⁇ 7.0% Fe, 1.0 ⁇ 8.5% Co, 1.0 ⁇ 8.0% Cu and one or more kinds. :! ⁇ 6.0% including A1, and further 0.:! ⁇ 4.0%V, 1.0 ⁇ 5.0% Sn, 1.5 ⁇ 6.0% Zr, 1.0 ⁇ 4. Examples include 1% or more of 0% Nb, 1.0 to 6.0% Mn, and Ti of 50% by weight or more, the balance inevitable substance, and a powerful alloy material.
- This sintered Ti alloy material is a sintered Ti alloy material that uses a liquid phase of one or more of Ti-Fe, Co, and Cu produced during the sintering process as a sintering promotion phase, In particular, it has excellent strength-toughness and a good balance between them.
- the manufacturing method of the high density sintered Ti alloy material of the present invention is as follows.
- sintering powder preparation step a molding process in which the sintering powder is molded into a predetermined shape to form a molded body, and the molded body is heated to a sintering temperature to form a liquid phase composed of Ti_Ni_B.
- NiB exists after sintering.
- the power S is necessary. Therefore, it is preferable to add B and Ni simultaneously in the form of NiB powder and Ni-B alloy powder, rather than adding B and Ni separately.
- the power of using NiB powder is particularly preferable.
- sintering powder preparation process first, Ti powder, one or more of Fe, Co, and Cu, and element powder or mother alloy powder containing B and Ni, and NiB as necessary, are prepared. In this step, these raw material powders are mixed to form a mixed powder (sintering powder) to be a forming raw material. Since a well-known powder unmixing method can be employed in this step, a uniform mixed powder of each raw material powder can be obtained without any special means.
- the next molding step is a step in which the prepared sintering powder is molded into a predetermined shape in a molding die or the like to obtain a molded body.
- the powder for sintering is formed by using a well-known metal powder forming method and under normal pressure, thereby easily obtaining a desired shape (green compact) with sufficient strength for handling. be able to.
- the next sintering step is a step of heating and sintering the obtained molded body. Sintering of the molded body can be performed in a normal temperature and time in a vacuum or in a protective (eg, inert atmosphere, reducing atmosphere) furnace.
- this manufacturing method is a manufacturing method that is in line with ordinary powder-free metal technology. Since readily available raw material powder and existing equipment can be used, high-density sintered Ti alloy materials can be manufactured at low cost.
- a sintering powder further containing at least one of Fe, Ni, Co, Cu, Al, V, Sn, Zr, Nb, and Mn can be obtained.
- Fe and Ni can be added as an alloy of Fe and Ni, or each constituent alloy element can be added as a boride. .
- the mechanism of the formation of a temporary liquid phase is affected in both cases of element powders and alloy powders as raw materials for sintering powders. Invite you. Therefore, the type of starting material is not limited.
- Fe_Ni alloy is a general material as a melting raw material, and is excellent in grindability, so no special melting method or grinding method is required.
- various boride powders are generally commercially available and do not require any special dissolution method. This makes it possible to obtain the desired sintered Ti alloy material at low cost without any special means.
- a sintered Ti alloy material in which at least one of Fe, Ni, Co, and Cu is contained in the sintered Ti alloy material of the present invention composed of Ti, B, and Ni has a high density, high rigidity, and high strength. Excellent properties such as strength and wear resistance.
- the temporary Ti_Fe, Co, and Cu that work effectively as a sintering-promoting phase at temperatures just below the sintering temperature. Since a dense sintered body can be obtained by forming a liquid phase of _Ni_B more than seeds, it is possible to exert excellent properties such as high rigidity, high strength, and wear resistance.
- the (/ 3 + ⁇ + Liquid) phase becomes stable at lower temperatures, so a high-density sintered Ti alloy material can be obtained in a short time. .
- Ti alloy is a material that is widely used in the fields of aviation, space, and military as a lightweight, high-strength material.
- manufacturing cost is remarkably high, there is no example applied to mass production parts, especially mass production dedicated parts that heavily use steel.
- mass production dedicated parts that heavily use steel.
- cost and characteristics such as low rigidity (about half) and inferior wear resistance compared to steel, it did not satisfy the needs of automotive part designers.
- the sintered Ti alloy material of the present invention can satisfy these needs. Therefore, the sintered Ti alloy material of the present invention can be applied to parts that impose such demands, such as automotive engine parts, various sports parts, tools, etc. It is. Specific application examples include automotive parts such as valpretainers, valve lifters, and connecting rods. Representative sports parts include golf heads, irons, and putters.
- Valve retainers, valve lifters, and connecting rods are required to have excellent cold, warm, and hot workability as well as mass productivity in the production process of automobile parts. Further, in order to satisfy the function, high strength, particularly high fatigue strength is required. Therefore, when the total is 100%, 0.6 to 4.8% NiB (0.3 to 2.4% after sintering), 1.0 to 7.0% Fe, 1.0 ⁇ 8.5% Co, 1. 0 ⁇ 8.0% Cu and one or more of 0.:! ⁇ 6.0%A1 In addition, a sintered Ti alloy material containing 0.1 to 4.0% V and further containing Ti of 50% or more and the balance inevitable substance is suitable.
- the composite material for blades is required to have antibacterial properties as well as excellent wear resistance. Therefore, when the total amount of the present invention is 100%, z is less than 0.6 to 4.8% NiB (0.3 to 2.4% before and after sintering), 1. 0 to 7.0% Fe, 1.0 to 8.5% Co, 1. 0 to 8.0% Cu, and 0.:! To 6.0% A1 and further 0 .:! ⁇ 4.0 Contains 0% V, force, one AgO. Contains 1 ⁇ 5 wt%, Ti is 50. Sintered Ti alloy material consisting of more than / o and the remainder of the inevitable substance is optimal.
- the alloy composition for obtaining a dense sintered Ti alloy material at a low temperature in a short time includes Fe, Ni, A sintered Ti alloy material containing at least one of Co and Cu is preferred.
- a sintered body of sintered Ti alloy material having a matrix mainly composed of Ti alloy and TiB dispersed and held in the matrix after disappearing after forming a liquid phase by heating.
- This sintering powder activates a temporary Ti-Ni_B liquid phase that works effectively as a sintering-promoting phase at a temperature just below the sintering temperature.
- High-density sintered Ti alloy material can be manufactured at low cost.
- any commercially available Ti powder may be used.
- powders such as sponge titanium powder, hydrodehydrogenated powder, titanium hydride powder, and atomized titanium powder can be used as received.
- the particle size of the powder is commercially available; most are adjusted to about 150 zm (_ # 100) or less.
- a Ti powder having a particle size of 45 zm or less is more preferable because it facilitates densification of the sintered body.
- B and Ni it is preferable to add B and Ni at the same time in the form of compound NiB powder or mixed powder of B and Ni, etc., rather than individually using the elemental powder of each element. I like it. It is particularly preferred to use NiB powder. This is because Ni atoms are present in the vicinity of the B atoms, so that NiB can be easily formed during sintering, and characteristics such as wear resistance can be reliably improved.
- one or more of Fe, Ni, Co, and Cu, one or more of V, Sn, Zr, Nb, and Mn, and element powder or mother alloy powder containing B and Ni are commercially available. Any of those prepared by a known method may be used.
- Fe and Ni may be added as an alloy of Fe and Ni. It is practical and desirable to add each constituent element as a boride.
- the alloy powder and boride powder of about several ⁇ . If a powder larger than that is obtained, the desired particle size can be obtained with various grinders such as a ball mill, a vibration mill, and an attritor. It is preferable to use after adjusting the powder.
- the mixing method used in the sintering powder preparation step is not particularly limited.
- a V-type mixer, a ball mill, a vibration mill, or the like can be used.
- the boride particle force is a highly agglomerated powder such as secondary particles
- the mixing process is activated in an inert gas atmosphere using a high energy ball mill such as an attritor to activate the densification. It is effective against
- any method may be used as long as a desired shape can be obtained, such as die molding, CIP molding, RIP molding, and SPS molding.
- the molding pressure is not particularly specified as long as the strength of the molded body sufficient for handling is obtained.
- the atmosphere is desirably an inert gas atmosphere in a vacuum.
- sintering is preferably performed at a temperature range of 1200 ° C to 1300 ° C for 1 to 16 hours. Good. When sintering for less than 1200 ° C and less than 1 hour, sufficient liquid phase necessary for densification is not supplied in the vicinity of the grain boundary, and for sintering exceeding 1300 ° C and for more than 16 hours, energy is required. It is uneconomical.
- hot working After the sintering step.
- HIP processing hot forging, extrusion, swaging, etc. are used.
- the processing temperature is preferably in the range of 700 to 1200 ° C. When machining below 700 ° C, the deformation resistance is too high. When exceeding 1200 ° C, the material properties after oxidation are severely affected, and fine cracks are formed on the surface during hot working. This is not preferable because there is a possibility.
- Ti powder (average particle size: 75 / m), Ni-B powder (NiB compound powder) (average particle size: 75 / im), Ag powder (average particle size: 50 / im) were prepared as raw material powders. .
- Ti powder, Ni-B powder, and Ag powder are blended in the proportions shown in Table 1 to form a powder for sintering, and this powder for sintering is molded into a shape of ⁇ 20 mm x 10 mm at a pressure of 3 ton / cm 2. Then, this molded body was sintered for 1 hr at 1300 ° C. in a vacuum of 1.3 ⁇ lCTPa. (Sample number: 1)
- Example 3 8 Compound 0.6 Compound Remainder 3 2 1 99 ⁇
- Example 3 11 Compound 2.7 Compound Remaining 0.05 1 1 96.7 A
- Example 3 15 Compound 0.5 Balance 3 2 1 97.4 ⁇
- Second comparative example G2 simple substance 2.7 Composite balance 3 2 0 93.1 X [0057] (Second embodiment)
- Ti powder (average particle size: 75 / m), A1 powder (average particle size: 75 / m), V powder (average particle size: 75 / im), Ni-B powder (NiB powder) ( Average particle size: 75 / im) and Ag powder (average particle size: 50 ⁇ m) were prepared.
- this compact was sintered at 1 300 ° C. in a vacuum of 1.3 ⁇ 10 3 Pa for 1 hr. (Sample number: 2)
- Alloy powder (average particle size: 75 ⁇ m), Ni-B powder (NiB powder) (average particle size: 75 ⁇ m), Ag powder (average particle size: 50 ⁇ m) made of Ti_Al_V as raw material powders did.
- Ti -A1-V alloy powder, Ni- B powder, the Ag powder is formulated in the ratio shown in Table 1 and sintered powder, the use sintered powder in the shape of phi 20 mm X 10 mm with a pressure 3TonZcm 2
- the molded body was then sintered in a vacuum of 1.3 X 10 3 Pa at 1300 ° C for lhr. (Sample number: 3 ⁇ : 16)
- Ti powder (average particle size: 75 / m), Ni powder (average particle size: 75 ⁇ m), and B powder (average particle size: 75 ⁇ m) were prepared as raw material powders.
- Ti powder, Ni powder, and B powder are blended in the proportions shown in Table 1 to form a powder for sintering.
- the powder for sintering is molded into a shape of ⁇ 20mm ⁇ 10mm at a pressure of 3ton / cm 2 , and then This molded body was sintered for 1 hr at 1300 ° C in a vacuum of 1.3 X 10 3 Pa. (Sample number: C1)
- alloy powder made of Ti_Al_V (average particle size: 75 ⁇ m), Ni powder (average particle size: 75 ⁇ m), and B powder (average particle size: 75 ⁇ m) were prepared.
- Ti_Al_V alloy powder, Ni powder, B powder, the Ag powder is formulated in the ratio shown in Table 1 and sintered powder, the shape of the sintering Powder in the pressure 3ton / cm 2 ⁇ 20mm X 10mm Then, this compact was sintered in a vacuum of 1.3 ⁇ 10 3 Pa at 1300 ° C. for lhr. (Sample number: C2)
- the sample was bladed to produce the blade, the blade edge of the blade was applied to the test paper under a constant load, and a reciprocating cycle motion of 30 mm one way at a constant speed was 128 reciprocations. It is possible to evaluate whether the test sheet is stable up to 128 times by adopting an evaluation method that records the number of cuts of the test paper every cycle.
- the abrasion resistance measurement method is based on the slope of the sharpness line up to 128 round trips with the logarithmic display on the horizontal axis.
- the Ti alloy material of the example according to the present invention has a high relative density of 97% or more and excellent wear resistance. It can be seen that wear resistance is obtained compared to the comparative example because the relative density is high and the hardness is increased by alloying.
- NiB powder composite shown in Table 1 means an alloy powder (NiB compound powder) in which Ni and B are reacted in advance, and the simple substance means that Ni and B are added as a single powder respectively.
- the Ti alloy powder composite shown in Table 1 means an alloy powder obtained by reacting Ti, A1, and V in advance, and the simple substance means adding Ti, A1, and V as a single powder, respectively. .
- This powder for sintering was formed into a shape of ⁇ 20 mm x 10 mm at a pressure of 3 ton Zcm 2 , and then this compact was sintered for 1 hr at 1300 ° C in a vacuum of 1.3 X 10 3 Pa. It was.
- Example 4 1200. Lhr sintering was performed at C. Also, for Example 4- 2 1. 3 X 10 3 Pa lhr at 1350 ° C in vacuum of, in vacuum of 1. 3 X 10 3 Pa for Example 4-3 1400. Lhr sintering was performed at C.
- each sample was transferred to a transmission electron microscope equipped with EELS (electron beam energy loss spectrometer) ( The structure was observed by TEM) and elemental mapping was performed using EELS.
- the phase in which Ti and B mainly exist is TiB phase
- the phase in which Ni and B mainly exist is NiB phase
- the phase in which Ti and Ni mainly exist is TiNi phase.
- the phases judged as TiB phase, NiB phase, and TiNi phase were analyzed by AES (Auger electron spectroscopy).
- Example 4-1 is the optimum condition of the present invention in which Al, V, Ag, CI, and Mo are merely in the above-described preferable range.
- TiB, TiNi, and NiB in the Ti alloy matrix were present in a well-balanced manner and had particularly excellent wear resistance.
- Samples 16 to 4-19 were also evaluated for antibacterial properties. Antibacterial activity was evaluated by measuring the incidence of fungi and mold of Legionella. The method for evaluating the incidence of fungi was evaluated according to the Japanese Industrial Standard CIIS) including the method for analyzing and measuring fungi and the method for cleaning assembled parts.
- CIIS Japanese Industrial Standard
- a mixed spore suspension of 5 types of mold was used based on the JISZ2911 mold resistance test method. After being collected from the culture surface cultured for 10 days in PSA medium, filtered and soaked in ethanol for 1 minute, the dried sample was attached to the actual product and cultured at 28 ° C and 95% relative humidity for 4 weeks. if the incidence of bacteria 10-2 or less and to have antibacterial properties.
- Legionella based on the JISZ2801 film adhesion method, Legionella is placed on the surface of the film, and the film is adhered to the actual surface. and that there is antibacterial if the number of bacteria 10 2 or less
- Examples 4_17 to 4_19 containing 0.1% or more of Ag exhibited excellent corrosion resistance against both mold and Legionella. However, if the amount of Ag exceeds 5%, the cost rises remarkably, so Ag is preferably 5% or less.
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JP2008517987A JP5153624B2 (ja) | 2006-05-31 | 2007-05-31 | 複合材料とその製造方法、ならびに、それに用いる組成物およびそれを用いた刃物 |
US12/302,442 US20090183598A1 (en) | 2006-05-31 | 2007-05-31 | Composite material , method for manufacturing the same, and edged tool by using the same |
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Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2010156035A (ja) * | 2008-12-30 | 2010-07-15 | Ind Technol Res Inst | 抗菌性合金コーティング組成物 |
WO2011152359A1 (ja) * | 2010-05-31 | 2011-12-08 | 東邦チタニウム株式会社 | セラミックスを含有したチタン合金複合粉およびその製造方法、これを用いた緻密化されたチタン合金材およびその製造方法 |
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 |
CN108679136A (zh) * | 2018-05-18 | 2018-10-19 | 宁波市奇强精密冲件有限公司 | 减震器弹簧盘 |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN113957288B (zh) * | 2021-09-18 | 2022-05-24 | 华南理工大学 | 一种低成本高性能的TiBw/Ti复合材料及其制备方法与应用 |
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JPH03193801A (ja) * | 1989-12-25 | 1991-08-23 | Nippon Steel Corp | 金属間化合物焼結添加用粉末および焼結法 |
JPH055142A (ja) * | 1990-11-30 | 1993-01-14 | Toyota Central Res & Dev Lab Inc | チタン基複合材料およびその製造方法 |
JPH10298611A (ja) * | 1997-04-25 | 1998-11-10 | Akira Hirai | 抗菌性焼結刃物 |
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US4968348A (en) * | 1988-07-29 | 1990-11-06 | Dynamet Technology, Inc. | Titanium diboride/titanium alloy metal matrix microcomposite material and process for powder metal cladding |
DE69128692T2 (de) * | 1990-11-09 | 1998-06-18 | Toyoda Chuo Kenkyusho Kk | Titanlegierung aus Sinterpulver und Verfahren zu deren Herstellung |
JP2796917B2 (ja) * | 1993-02-02 | 1998-09-10 | 株式会社クボタ | 耐食耐摩耗性等にすぐれた非鉄金属溶湯部材用複合焼結合金 |
JPH08311586A (ja) * | 1995-05-16 | 1996-11-26 | Maruto Hasegawa Kosakusho:Kk | α,β二相チタン合金複合材料並びに各種製品のチタン合金材料とチタン合金製品 |
JP4772388B2 (ja) * | 2004-06-25 | 2011-09-14 | 株式会社クボタ | ダイカストマシン用プランジャーチップ |
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- 2007-05-31 JP JP2008517987A patent/JP5153624B2/ja active Active
- 2007-05-31 WO PCT/JP2007/061118 patent/WO2007139194A1/ja active Application Filing
- 2007-05-31 US US12/302,442 patent/US20090183598A1/en not_active Abandoned
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JPH03193801A (ja) * | 1989-12-25 | 1991-08-23 | Nippon Steel Corp | 金属間化合物焼結添加用粉末および焼結法 |
JPH055142A (ja) * | 1990-11-30 | 1993-01-14 | Toyota Central Res & Dev Lab Inc | チタン基複合材料およびその製造方法 |
JPH10298611A (ja) * | 1997-04-25 | 1998-11-10 | Akira Hirai | 抗菌性焼結刃物 |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2010156035A (ja) * | 2008-12-30 | 2010-07-15 | Ind Technol Res Inst | 抗菌性合金コーティング組成物 |
WO2011152359A1 (ja) * | 2010-05-31 | 2011-12-08 | 東邦チタニウム株式会社 | セラミックスを含有したチタン合金複合粉およびその製造方法、これを用いた緻密化されたチタン合金材およびその製造方法 |
JPWO2011152359A1 (ja) * | 2010-05-31 | 2013-08-01 | 東邦チタニウム株式会社 | セラミックスを含有したチタン合金複合粉およびその製造方法、これを用いた緻密化されたチタン合金材およびその製造方法 |
JP5855565B2 (ja) * | 2010-05-31 | 2016-02-09 | 東邦チタニウム株式会社 | セラミックスを含有したチタン合金混合粉、これを用いた緻密化されたチタン合金材およびその製造方法 |
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 |
CN108679136A (zh) * | 2018-05-18 | 2018-10-19 | 宁波市奇强精密冲件有限公司 | 减震器弹簧盘 |
CN108679136B (zh) * | 2018-05-18 | 2020-01-31 | 宁波市奇强精密冲件有限公司 | 减震器弹簧盘 |
Also Published As
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US20090183598A1 (en) | 2009-07-23 |
JP5153624B2 (ja) | 2013-02-27 |
JPWO2007139194A1 (ja) | 2009-10-15 |
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