Patent Grant
7578866
This is a U.S. national phase application under 35 U.S.C. §371 of International Patent Application No. PCT/JP2004/003094 filed Mar. 10, 2004, and claims the benefit of Japanese Patent Application No. 2003-62854 filed Mar. 10, 2003 which is incorporated by reference herein. The International Application published in Japanese on Sep. 23, 2004 as WO 2004/003094 A1 under PCT Article 21(2).
The present invention relates to an iron-based sintered alloy having excellent machinability which is used as materials for various machine components.
With the progress of a sintering technique, various electric components such as yoke and rotor, and various machine components such as pistons for shock absorber, rod guides, bearing caps, valve plates for compressor, hubs, forkshifts, sprockets, toothed wheels, gears and synchronizer hubs have recently been produced using an iron-based sintered alloy obtained by sintering a raw powder mixture. For example, it is known that an iron-based sintered alloy having the composition consisting of pure iron and 0.1 to 1.5% by mass of P, the balance being Fe and inevitable impurities, is used to produce various electric components such as yokes and rotors. It is known that an iron-based sintered alloy having the composition consisting of 0.1 to 1.2% by mass of C, the balance being Fe and inevitable impurities, is used to produce pistons for shock absorber, and lot guides. It is known that an iron-based sintered alloy having the composition consisting of 0.1 to 1.2% by mass of C and 10 to 25% by mass of Cu, the balance being Fe and inevitable impurities, is used to produce bearing caps, and valve plates for compressor. It is known that an iron-based sintered alloy having the composition consisting of 0.1 to 1.2% by mass of C and 0.1 to 6% by mass of Cu, the balance being Fe and inevitable impurities, is used to produce forkshifts, sprockets, gears, toothed wheels, and pistons for shock absorber. It is known that an iron-based sintered alloy having the composition consisting of 0.1 to 1.2% by mass of C, 0.1 to 6% by mass of Cu, 0.1 to 10% by mass of Ni and 0.1 to 6% by mass of Mo, the balance being Fe and inevitable impurities, is used to produce CL cranks, sprockets, gears, and toothed wheels.
It is known that an iron-based sintered alloy having the composition consisting of 0.1 to 1.2% by mass of C and 0.1 to 6% by mass of Mo, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 0.1 to 1.2% by mass of C, 0.1 to 10% by mass of Cr and 0.1 to 6% by mass of Mo, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 0.1 to 1.2% by mass of C, 0.1 to 10% by mass of Ni, 0.1 to 10% by mass of Cr and 0.1 to 6% by mass of Mo, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 0.1 to 1.2% by mass of C, 0.1 to 6% by mass of Cu, 0.1 to 10% by mass of Ni, 0.1 to 10% by mass of Cr and 0.1 to 6% by mass of Mo, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 0.1 to 1.2% by mass of C and 0.1 to 10% by mass of Ni, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 0.1 to 1.2% by mass of C, 0.1 to 10% by mass of Ni and 0.1 to 6% by mass of Mo, the balance being Fe and inevitable impurities, and an iron-based sintered alloy having the composition consisting of 0.1 to 1.2% by mass of C, 0.1 to 6% by mass of Cu and 0.1 to 10% by mass of Ni, the balance being Fe and inevitable impurities, are used as materials of various machine components such as sprockets, gears and toothed wheels.
Also it is known that an iron-based sintered alloy having the composition consisting of 1.0 to 3.0% by mass of C, 0.5 to 8% by mass of Cu and 0.1 to 0.8% by mass of P, the balance being Fe and inevitable impurities, are used as materials of valve guides.
Also it is known that an iron-based sintered alloy having the composition consisting of 0.3 to 2.5% by mass of C, 0.5 to 12% by mass of Cr, 0.3 to 9% by mass of Mo, 3 to 14% by mass of W and 1 to 6% by mass of V, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 0.3 to 2.5% by mass of C, 0.5 to 12% by mass of Cr, 0.3 to 9% by mass of Mo, 3 to 14% by mass of W, 1 to 6% by mass of V and 5 to 14% by mass of Co, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 0.3 to 2% by mass of C, 0.5 to 10% by mass of Cr, 0.3 to 16% by mass of Mo and 0.1 to 5% by mass of Ni, and one or more kinds selected from among 1 to 5% by mass of W, 0.05 to 1% by mass of Si, 0.5 to 18% by mass of Co and 0.05 to 2% by mass of Nb, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 0.3 to 2% by mass of C, 0.5 to 10% by mass of Cr, 0.3 to 16% by mass of Mo and 0.1 to 5% by mass of Ni, one or more kinds selected from among 1 to 5% by mass of W, 0.05 to 1% by mass of Si, 0.5 to 18% by mass of Co and 0.05 to 2% by mass of Nb, and 10 to 20% by mass of Cu, the balance being Fe and inevitable impurities, and an iron-based sintered alloy having the composition consisting of 0.3 to 2% by mass of C, 0.1 to 3% by mass of Mo, 0.05 to 5% by mass of Ni and 0.1 to 2% by mass of Co, the balance being Fe and inevitable impurities, are used as materials of valve seats.
Also it is known that an iron-based sintered alloy having the composition consisting of 15 to 27% by mass of Cr and 3 to 29% by mass of Ni, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of one or more kinds selected from among 15 to 27% by mass of Cr, 3 to 29% by mass of Ni, 0.5 to 7% by mass of Mo and 0.5 to 4% by mass of Cu, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 10 to 33% by mass of Cr, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 10 to 33% by mass of Cr and 0.5 to 3% by mass of Mo, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 10 to 33% by mass of Cr and 0.5 to 3% by mass of Mo, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 10 to 19% by mass of Cr and 0.05 to 1.3% by mass of C, the balance being Fe and inevitable impurities, an iron-based sintered alloy having the composition consisting of 14 to 19% by mass of Cr and 2 to 8% by mass of Ni, the balance being Fe and inevitable impurities, and an iron-based sintered alloy having the composition consisting of 14 to 19% by mass of Cr and 2 to 8% by mass of Ni, and one or more kinds selected from among 2 to 6% by mass of Cu, 0.1 to 0.5% by mass of Nb and 0.5 to 1.5% by mass of Al, the balance being Fe and inevitable impurities, are used as materials of corrosion-resistant machine components.
Various machine components made of these conventional iron-based sintered alloys are produced by blending predetermined raw powders, mixing the powders and compacting the powder mixture to obtain a green compact, and sintering the resulting green compact in a vacuum, dissociated ammonia gas, N2+5% H2 gas mixture, endothermic gas or exothermic gas atmosphere, and are finally shipped after piercing the required position using a drill and cutting or grinding the surface. Machining such as piercing, cutting or grinding is conducted by using various cutting tools. When machine components have a lot of positions to be cut, cutting tools are drastically worn out, resulting in high cost. Therefore, there has been made a trial of suppressing wear of the cutting tool by a method of adding about 1% of a MnS or MnO powder and sintering the resulting green compact thereby to improve machinability of the cutting tool (see Japanese Patent Application, First Publication No. Hei 3-267354) or a method of adding a CaO—MgO—SiO2-based complex oxide, thereby to improve machinability (see Japanese Patent Application, First Publication No. Hei 8-260113) of the cutting tool, and thus reducing the cost.
An iron-based sintered alloy obtained by adding a conventional MnS powder, MnO powder or CaO—MgO—SiO2-based complex oxide powder and sintering the resulting green compact has machinability, which is improved to some extent, but is not still satisfactory. Therefore, it is required to develop an iron-based sintered alloy having more excellent machinability.
From such a point of view, the present inventors have intensively studied so as to obtain an iron-based sintered alloy having more excellent machinability, which can be used as materials of various electric and machine components. As a result, they have found that an iron-based sintered alloy containing 0.05 to 3% by mass of a calcium carbonate powder or an iron-based sintered alloy containing 0.05 to 3% by mass of a strontium carbonate powder has more improved machinability.
The present invention has been made based on such a finding and is characterized by the followings:
The iron-based sintered alloys having excellent machinability, which contain 0.05 to 3% by mass of calcium carbonate, according to (1) to (27) of the present invention are produced by blending a calcium carbonate powder having an average particle size of 0.1 to 30 μm with raw powders, mixing these powders and compacting the powder mixture to obtain a green compact, and sintering the resulting green compact in an atmosphere of a nonoxidizing gas such as vacuum, dissociated ammonia gas, N2+5% H2 gas mixture, endothermic gas or exothermic gas. The green compact is particularly preferably sintered in an atmosphere of the nonoxidizing gas such as endothermic gas or exothermic gas. The iron-based sintered alloy thus obtained has a structure in which CaCO3 is dispersed at grain boundary in a basis material of the iron-based sintered alloy. The presence of CaCO3 in the sintered compact obtained by sintering the green compact can be confirmed by X-ray diffraction.
The iron-based sintered alloys having excellent machinability, which contain 0.05 to 3% by mass of strontium carbonate, according to (28) to (54) of the present invention are produced by blending a strontium carbonate powder having an average particle size of 0.1 to 30 μm with raw powders, mixing these powders and compacting the powder mixture to obtain a green compact, and sintering the resulting green compact in an atmosphere of a nonoxidizing gas such as vacuum, dissociated ammonia gas, N2+5% H2 gas mixture, endothermic gas or exothermic gas. The green compact is particularly preferably sintered in an atmosphere of the nonoxidizing gas such as endothermic gas or exothermic gas. The iron-based sintered alloy thus obtained has a structure in which SrCO3 is dispersed at grain boundary in a basis material of the iron-based sintered alloy. The presence of SrCO3 in the sintered compact obtained by sintering the green compact can be confirmed by X-ray diffraction.
Therefore, the present invention is characterized by the followings: (55) a method for preparing the iron-based sintered alloy having excellent machinability according to any one of (1) to (27), which comprises compacting a raw powder mixture containing 0.05 to 3% by mass of a calcium carbonate powder having an average particle size of 0.1 to 30 μm as a raw powder to obtain a green compact and sintering the resulting green compact in a nonoxidizing gas atmosphere, and (56) a method for preparing the iron-based sintered alloy having excellent machinability according to any one of (28) to (54), which comprises compacting a raw powder mixture containing 0.05 to 3% by mass of a strontium carbonate powder having an average particle size of 0.1 to 30 μm as a raw powder to obtain a green compact and sintering the resulting green compact in a nonoxidizing gas atmosphere.
The average particle size of the calcium carbonate powder as the raw powder was defined within a range from 0.1 to 30 μm by the following reason. That is, when the average particle size of the calcium carbonate powder exceeds 30 μm, a contact area between the calcium carbonate powder and the basis material decreases and sufficient machinability improving effect is not exerted. On the other hand, when the average particle size of the calcium carbonate powder is less than 0.1 μm, a force of agglomeration increases, and thus the calcium carbonate powder is not uniformly dispersed in the basis material and further machinability improving effect is not exerted, and it is not preferred.
The average particle size of the strontium carbonate powder as the raw powder was defined within a range from 0.1 to 30 μm by the following reason. That is, when the average particle size of the strontium carbonate powder exceeds 30 μm, a contact area between the strontium carbonate powder and the basis material decreases and sufficient machinability improving effect is not exerted. On the other hand, when the average particle size of the strontium carbonate powder is less than 0.1 μm, a force of agglomeration increases, and thus the strontium carbonate powder is not uniformly dispersed in the basis material and further machinability improving effect is not exerted, and it is not preferred.
The endothermic gas is a gas containing, as a main component, hydrogen, carbon monoxide and nitrogen, which is obtained by mixing a natural gas, propane, butane or coke oven gas with an air to obtain a gas mixture, and decomposing and converting the gas mixture while passing through a heated catalyst composed mainly of nickel. In this case, since this reaction is an endothermic reaction, a catalyst layer must be heated. The exothermic gas is a gas containing nitrogen as a main component, hydrogen and carbon monoxide, which is obtained by semicombusting a natural gas, propane, butane or coke oven gas with air, and decomposing and converting the combustion gas while passing through a nickel catalyst layer or charcoal layer. In this case, since the temperature of the catalyst increases due to combustion heat of the raw gas, it is not necessary to externally heat the catalyst layer.
The sintering temperature, at which the iron-based sintered alloy having excellent machinability is sintered, is preferably from 1100 to 1300° C. (more preferably from 1110 to 1250° C.) and this sintering temperature is the temperature which is generally known as a temperature at which the iron-based sintered alloy is sintered.
The reason why the composition of the CaCO3 component and the composition of the SrCO3 component in the iron-based sintered alloy having excellent machinability of the present invention were as limited as described above will now be described.
CaCO3 has such an effect that it exists at grain boundary and is uniformly dispersed in a basis material, thereby to improve machinability. When the content is less than 0.05% by mass, sufficient machinability improving effect is not exerted. On the other hand, even when the content exceeds 3.0% by mass, further machinability improving effect is not exerted and the strength of the iron-based sintered alloy rather decreases, and therefore it is not preferred. Therefore, the content of CaCO3 in the iron-based sintered alloy of the present invention was defined within a range from 0.05 to 3.0% by mass. The content of CaCO3 is more preferably within a range from 0.1 to 2% by mass.
SrCO3 has such an effect that it exists at grain boundary and is uniformly dispersed in a basis material, thereby to improve machinability. When the content is less than 0.05% by mass, sufficient machinability improving effect is not exerted. On the other hand, even when the content exceeds 3.0% by mass, further machinability improving effect is not exerted and the strength of the iron-based sintered alloy rather decreases, and therefore it is not preferred. Therefore, the content of SrCO3 in the iron-based sintered alloy of the present invention was defined within a range from 0.05 to 3.0% by mass. The content of SrCO3 is more preferably within a range from 0.1 to 2% by mass.
Preferred examples of the present invention will now be described with reference to the accompanying drawings. The present invention is not limited to the following examples and, for example, constituent features of these examples may be appropriately combined with each other.
As raw powders, a CaCO3 powder having an average particle size shown in Table 1, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm and a pure Fe powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 1, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 1 to 10 of the present invention, comparative sintered alloys 1 to 2, and conventional sintered alloys 1 to 3.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 1 to 10 of the present invention, the comparative sintered alloys 1 to 2, and the conventional sintered alloys 1 to 3 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 1, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 1 to 10 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 1 to 3 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 1 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 2 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 2, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm and a Fe-0.6 mass % P powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 2, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 11 to 20 of the present invention, comparative sintered alloys 3 to 4, and conventional sintered alloys 4 to 6.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 11 to 20 of the present invention, the comparative sintered alloys 3 to 4, and the conventional sintered alloys 4 to 6 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 2, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 11 to 20 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 4 to 6 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 3 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 4 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 3, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm, a Fe powder having an average particle size of 80 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 3, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 21 to 30 of the present invention, comparative sintered alloys 5 to 6, and conventional sintered alloys 7 to 9.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 21 to 30 of the present invention, the comparative sintered alloys 5 to 6, and the conventional sintered alloys 7 to 9 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 3, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 21 to 30 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 7 to 9 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 5 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 6 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 4, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm, a Fe powder having an average particle size of 80 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 4, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes and subjected to 20% Cu infiltration to obtain iron-based sintered alloys 31 to 40 of the present invention, comparative sintered alloys 7 to 8, and conventional sintered alloys 10 to 12.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 31 to 40 of the present invention, the comparative sintered alloys 7 to 8, and the conventional sintered alloys 10 to 12 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 4, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 31 to 40 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 10 to 12 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 7 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 8 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 5, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm, a Fe powder having an average particle size of 80 μm, a Cu powder having an average particle size of 25 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 5, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 41 to 50 of the present invention, comparative sintered alloys 9 to 10, and conventional sintered alloys 13 to 15.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 41 to 50 of the present invention, the comparative sintered alloys 9 to 10, and the conventional sintered alloys 13 to 15 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 5, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 41 to 50 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 13 to 15 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 9 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 10 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 6, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm, a partially diffused Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-1.5% Cu-4.0% Ni-0.5% Mo and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 6, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 51 to 60 of the present invention, comparative sintered alloys 11 to 12, and conventional sintered alloys 16 to 18.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 51 to 60 of the present invention, the comparative sintered alloys 11 to 12, and the conventional sintered alloys 16 to 18 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 6, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 51 to 60 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 16 to 18 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 11 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 12 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 7, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm, a Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-1.5% Mo and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 7, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 61 to 70 of the present invention, comparative sintered alloys 13 to 14, and conventional sintered alloys 19 to 21.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 61 to 70 of the present invention, the comparative sintered alloys 13 to 14, and the conventional sintered alloys 19 to 21 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 7, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 61 to 70 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 19 to 21 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 13 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 14 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 8, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm, a Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-3.0% Cr-0.5% Mo and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 8, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an N2+5% H2 gas mixture atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 71 to 80 of the present invention, comparative sintered alloys 15 to 16, and conventional sintered alloys 22 to 24.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 71 to 80 of the present invention, the comparative sintered alloys 15 to 16, and the conventional sintered alloys 22 to 24 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 8, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 71 to 80 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 22 to 24 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 15 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 16 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 9, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm, a Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-3.0% Cr-0.5% Mo, a Ni powder having an average particle size of 3 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 9, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an N2+5% H2 gas mixture atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 81 to 90 of the present invention, comparative sintered alloys 17 to 18, and conventional sintered alloys 25 to 27.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 81 to 90 of the present invention, the comparative sintered alloys 17 to 18, and the conventional sintered alloys 25 to 27 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 9, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 81 to 90 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 25 to 27 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 17 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 18 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 10, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm, a Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-3.0% Cr-0.5% Mo, a Cu powder having an average particle size of 25 μm, a Ni powder having an average particle size of 3 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 10, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an N2+5% H2 gas mixture atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 91 to 100 of the present invention, comparative sintered alloys 19 to 20, and conventional sintered alloys 28 to 30.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 91 to 100 of the present invention, the comparative sintered alloys 19 to 20, and the conventional sintered alloys 28 to 30 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 10, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 91 to 100 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 28 to 30 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 19 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 20 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 11, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm, a Fe powder having an average particle size of 80 μm, a Ni powder having an average particle size of 3 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 11, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 101 to 110 of the present invention, comparative sintered alloys 21 to 22, and conventional sintered alloys 31 to 33.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 101 to 110 of the present invention, the comparative sintered alloys 21 to 22, and the conventional sintered alloys 31 to 33 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 11, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 101 to 110 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 31 to 33 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 21 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 22 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 12, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm, a Fe powder having an average particle size of 80 μm, a Ni powder having an average particle size of 3 μm, a Mo powder having an average particle size of 3 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 12, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 111 to 120 of the present invention, comparative sintered alloys 23 to 24, and conventional sintered alloys 34 to 36.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 111 to 120 of the present invention, the comparative sintered alloys 23 to 24, and the conventional sintered alloys 34 to 36 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 12, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 111 to 120 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 34 to 36 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 23 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 24 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 13, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm, a Fe powder having an average particle size of 80 μm, a Ni powder having an average particle size of 3 μm, a Cu powder having an average particle size of 25 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 13, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 121 to 130 of the present invention, comparative sintered alloys 25 to 26, and conventional sintered alloys 37 to 39.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 121 to 130 of the present invention, the comparative sintered alloys 25 to 26, and the conventional sintered alloys 37 to 39 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 13, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 121 to 130 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 37 to 39 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 25 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 26 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size shown in Table 14, a CaMgSiO4 powder having an average particle size of 10 μm, a MnS powder having an average particle size of 20 μm, a CaF2 powder having an average particle size of 36 μm, a Fe powder having an average particle size of 80 μm, a Cu—P powder having an average particle size of 25 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 14, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 131 to 140 of the present invention, comparative sintered alloys 27 to 28, and conventional sintered alloys 40 to 42.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 131 to 140 of the present invention, the comparative sintered alloys 27 to 28, and the conventional sintered alloys 40 to 42 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 14, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 131 to 140 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 40 to 42 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 27 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 28 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size of 0.6 μm, a CaF2 powder having an average particle size of 36 μm and a Fe-6% Cr-6% Mo-9% W-3% V-10% Co-1.5% C powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 15, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a dissociated ammonia gas atmosphere under the conditions of a temperature of 1150° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 141 of the present invention, comparative sintered alloys 29 to 30, and a conventional sintered alloy 43.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 141 of the present invention, the comparative sintered alloys 29 to 30, and the conventional sintered alloy 43 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 15, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 141 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 43 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 29 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 30 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size of 0.6 μm, a CaF2 powder having an average particle size of 36 μm, a Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-13% Cr-5% Nb-0.8% Si, a Fe powder having an average particle size of 80 μm, a Ni powder having an average particle size of 3 μm, a Mo powder having an average particle size of 3 μm, a Co-based alloy powder having an average particle size of 80 μm with the composition of Co-30% Mo-10% Cr-3% Si, a Cr-based alloy powder having an average particle size of 80 μm with the composition of Cr-25% Co-25% W-11.5% Fe-1% Nb-1% Si-1.5% C, a Co powder having an average particle size of 30 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 16-1, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1150° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 142 of the present invention, comparative sintered alloys 31 to 32, and a conventional sintered alloy 44 shown in Table 16-2.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 142 of the present invention, the comparative sintered alloys 31 to 32, and the conventional sintered alloy 44 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 16-1 and Table 16-2, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 142 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 44 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 31 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 32 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size of 0.6 μm, a CaF2 powder having an average particle size of 36 μm, a Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-13% Cr-5% Nb-0.8% Si, a Fe powder having an average particle size of 80 μm, a Ni powder having an average particle size of 3 μm, a Mo powder having an average particle size of 3 μm, a Co-based alloy powder having an average particle size of 80 μm with the composition of Co-30% Mo-10% Cr-3% Si, a Cr-based alloy powder having an average particle size of 80 μm with the composition of Cr-25% Co-25% W-11.5% Fe-1% Nb-1% Si-1.5% C, a Co powder having an average particle size of 30 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 17-1, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1150° C. and a retention time of 60 minutes and subjected to 18% Cu infiltration to obtain an iron-based sintered alloy 143 of the present invention, comparative sintered alloys 33 to 34, and a conventional sintered alloy 45 shown in Table 17-2.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 143 of the present invention, the comparative sintered alloys 33 to 34, and the conventional sintered alloy 45 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 17-1 and Table 17-2, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 143 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 45 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 33 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 34 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size of 0.6 μm, a CaF2 powder having an average particle size of 36 μm, a Fe powder having an average particle size of 80 μm, a Ni powder having an average particle size of 3 μm, a Mo powder having an average particle size of 3 μm, a Co powder having an average particle size of 30 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 18-1, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1150° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 144 of the present invention, comparative sintered alloys 35 to 36, and a conventional sintered alloy 46 shown in Table 18-2.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 144 of the present invention, the comparative sintered alloys 35 to 36, and the conventional sintered alloy 46 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 18-1 and Table 18-2, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 144 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 46 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 35 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 36 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size of 0.6 μm, a CaF2 powder having an average particle size of 36 μm and a SUS316 (Fe-17% Cr-12% Ni-2.5% Mo) powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 19, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1200° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 145 of the present invention, comparative sintered alloys 37 to 38, and a conventional sintered alloy 47.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 145 of the present invention, the comparative sintered alloys 37 to 38, and the conventional sintered alloy 47 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 19, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 145 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 47 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 37 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 38 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size of 0.6 μm, a CaF2 powder having an average particle size of 36 μm and a SUS430 (Fe-17% Cr) powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 20, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1200° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 146 of the present invention, comparative sintered alloys 39 to 40, and a conventional sintered alloy 48.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 146 of the present invention, the comparative sintered alloys 39 to 40, and the conventional sintered alloy 48 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 20, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 146 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 48 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 39 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 40 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size of 0.6 μm, a CaF2 powder having an average particle size of 36 μm, a C powder having an average particle size of 18 μm and a SUS410 (Fe-13% Cr) powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 21, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1200° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 147 of the present invention, comparative sintered alloys 41 to 42, and a conventional sintered alloy 49.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 147 of the present invention, the comparative sintered alloys 41 to 42, and the conventional sintered alloy 49 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 21, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 147 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 49 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 41 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 42 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a CaCO3 powder having an average particle size of 0.6 μm, a CaF2 powder having an average particle size of 36 μm and a SUS630 (Fe-17% Cr-4% Ni-4% Cu-0.3% Nb) powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 22, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1200° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 148 of the present invention, comparative sintered alloys 43 to 44, and a conventional sintered alloy 50.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 148 of the present invention, the comparative sintered alloys 43 to 44, and the conventional sintered alloy 50 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 22, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 148 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 50 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 43 containing CaCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 44 containing CaCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 23 and a pure Fe powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 23, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 149 to 158 of the present invention and comparative sintered alloys 45 to 46.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 149 to 158 of the present invention and the comparative sintered alloys 45 to 46 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 23, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 149 to 158 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 1 to 3 shown in Table 1 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 45 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 46 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 24 and a Fe-0.6 mass % P powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 24, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 159 to 168 of the present invention and comparative sintered alloys 47 to 48.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 159 to 168 of the present invention and the comparative sintered alloys 47 to 48 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 24, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 159 to 168 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 4 to 6 shown in Table 2 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 47 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 48 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 25, a Fe powder having an average particle size of 80 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 25, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 169 to 178 of the present invention and comparative sintered alloys 49 to 50.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 169 to 178 of the present invention and the comparative sintered alloys 49 to 50 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 25, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 169 to 178 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 7 to 9 shown in Table 3 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 49 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 50 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 26, a Fe powder having an average particle size of 80 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 26, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes and subjected to 20% Cu infiltration to obtain iron-based sintered alloys 179 to 188 of the present invention and comparative sintered alloys 51 to 52.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 179 to 188 of the present invention and the comparative sintered alloys 51 to 52 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 26, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 179 to 188 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 10 to 12 shown in Table 4 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 51 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 52 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 27, a Fe powder having an average particle size of 80 μm, a Cu powder having an average particle size of 25 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 27, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 189 to 198 of the present invention and comparative sintered alloys 53 to 54.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 189 to 198 of the present invention and the comparative sintered alloys 53 to 54 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 27, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 189 to 198 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 13 to 15 shown in Table 5 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 53 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 54 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 28, a partially diffused Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-1.5% Cu-4.0% Ni-0.5% Mo and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 28, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 199 to 208 of the present invention and comparative sintered alloys 55 to 56.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 199 to 208 of the present invention and the comparative sintered alloys 55 to 56 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 28, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 199 to 208 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 16 to 18 shown in Table 6 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 55 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 56 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 29, a Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-1.5% Mo and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 29, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 209 to 218 of the present invention and comparative sintered alloys 57 to 58.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 209 to 218 of the present invention and the comparative sintered alloys 57 to 58 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 29, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 209 to 218 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 19 to 21 shown in Table 7 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 57 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 58 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 30, a Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-3.0% Cr-0.5% Mo and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 30, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an N2+5% H2 gas mixture under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 219 to 228 of the present invention and comparative sintered alloys 59 to 60.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 219 to 228 of the present invention and the comparative sintered alloys 59 to 60 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 30, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 219 to 228 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 22 to 24 shown in Table 8 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 59 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 60 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 31, a Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-3.0% Cr-0.5% Mo, a Ni powder having an average particle size of 3 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 31, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an N2+5% H2 gas mixture under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 229 to 238 of the present invention and comparative sintered alloys 61 to 62.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 229 to 238 of the present invention and the comparative sintered alloys 61 to 62 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 31, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 229 to 238 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 25 to 27 shown in Table 9 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 61 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 62 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 32, a Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-3.0% Cr-0.5% Mo, a Cu powder having an average particle size of 25 μm, a Ni powder having an average particle size of 3 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 32, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an N2+5% H2 gas mixture under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 239 to 248 of the present invention and comparative sintered alloys 63 to 64.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 239 to 248 of the present invention and the comparative sintered alloys 63 to 64 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 32, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 239 to 248 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 28 to 30 shown in Table 10 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 63 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 64 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 33, a Fe powder having an average particle size of 80 μm, a Ni powder having an average particle size of 3 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 33, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 249 to 258 of the present invention and comparative sintered alloys 65 to 66.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 249 to 258 of the present invention and the comparative sintered alloys 65 to 66 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 33, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 249 to 258 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 31 to 33 shown in Table 11 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 65 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 66 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 34, a Fe powder having an average particle size of 80 μm, a Ni powder having an average particle size of 3 μm, a Mo powder having an average particle size of 3 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 34, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 259 to 268 of the present invention and comparative sintered alloys 67 to 68. Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 259 to 268 of the present invention and the comparative sintered alloys 67 to 68 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 34, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 259 to 268 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 34 to 36 shown in Table 12 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 67 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 68 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size shown in Table 35, a Fe powder having an average particle size of 80 μm, a Ni powder having an average particle size of 3 μm, a Cu powder having an average particle size of 25 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 35, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 269 to 278 of the present invention and comparative sintered alloys 69 to 70.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 269 to 278 of the present invention and the comparative sintered alloys 69 to 70 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 35, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 269 to 278 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 37 to 39 shown in Table 13 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 69 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 70 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred
As raw powders, a SrCO3 powder having an average particle size shown in Table 36, a Fe powder having an average particle size of 80 μm, a Cu—P powder having an average particle size of 25 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 36, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in an endothermic gas (ratio of components=H2: 40.5%, CO: 19.8%, CO2: 0.1%, CH: 0.5%, and N2: 39.1%) atmosphere under the conditions of a temperature of 1120° C. and a retention time of 20 minutes to obtain iron-based sintered alloys 279 to 288 of the present invention and comparative sintered alloys 71 to 72.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloys 279 to 288 of the present invention and the comparative sintered alloys 71 to 72 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 36, the number of piercing of the cylindrical sintered alloy blocks for piercing test made of the sintered alloys 279 to 288 of the present invention is larger than that of the cylindrical sintered alloy blocks for piercing test made of the conventional sintered alloys 40 to 42 shown in Table 14 and therefore the sintered alloys of the present invention are excellent in machinability. However, the comparative sintered alloy 71 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 72 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size of 1 μm and a Fe-6% Cr-6% Mo-9% W-3% V-10% Co-1.5% C powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 37, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a dissociated ammonia gas atmosphere under the conditions of a temperature of 1150° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 289 of the present invention and comparative sintered alloys 73 to 74.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 289 of the present invention and the comparative sintered alloys 73 to 74 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 37, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 289 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 43 shown in Table 15 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 73 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 74 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size of 1 μm, a Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-13% Cr-5% Nb-0.8% Si, a Fe powder having an average particle size of 80 μm, a Ni powder having an average particle size of 3 μm, a Mo powder having an average particle size of 3 μm, a Co-based alloy powder having an average particle size of 80 μm with the composition of Co-30% Mo-10% Cr-3% Si, a Cr-based alloy powder having an average particle size of 80 μm with the composition of Cr-25% Co-25% W-11.5% Fe-1% Nb-1% Si-1.5% C, a Co powder having an average particle size of 30 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 38-1, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1150° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 290 of the present invention and comparative sintered alloys 75 to 76 shown in Table 38-2.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 290 of the present invention and the comparative sintered alloys 75 to 76 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 38-1 and Table 38-2, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 290 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 44 shown in Table 16-1 to Table 16-2 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 75 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 76 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size of 1 μm, a Fe-based alloy powder having an average particle size of 80 μm with the composition of Fe-13% Cr-5% Nb-0.8% Si, a Fe powder having an average particle size of 80 μm, a Ni powder having an average particle size of 3 μm, a Mo powder having an average particle size of 3 μm, a Co-based alloy powder having an average particle size of 80 μm with the composition of Co-30% Mo-10% Cr-3% Si, a Cr-based alloy powder having an average particle size of 80 μm with the composition of Cr-25% Co-25% W-11.5% Fe-1% Nb-1% Si-1.5% C, a Co powder having an average particle size of 30 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 39-1, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1150° C. and a retention time of 60 minutes and subjected to 18% Cu infiltration to obtain an iron-based sintered alloy 291 of the present invention and comparative sintered alloys 77 to 78 shown in Table 39-2.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 291 of the present invention and the comparative sintered alloys 77 to 78 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 39-1 and Table 39-2, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 291 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 45 shown in Table 17-1 to Table 17-2 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 77 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 78 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size of 1 μm, a Fe powder having an average particle size of 80 μm, a Ni powder having an average particle size of 3 μm, a Mo powder having an average particle size of 3 μm, a Co powder having an average particle size of 30 μm and a C powder having an average particle size of 18 μm were prepared. These raw powders were blended according to the formulation shown in Table 40-1, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1150° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 292 of the present invention and comparative sintered alloys 79 to 80 shown in Table 40-2.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 292 of the present invention and the comparative sintered alloys 79 to 80 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 40-1 and Table 40-2, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 292 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 46 shown in Table 18-1 to Table 18-2 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 79 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 80 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size of 1 μm and a SUS316 (Fe-17% Cr-12% Ni-2.5% Mo) powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 41, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1200° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 293 of the present invention and comparative sintered alloys 81 to 82.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 293 of the present invention and the comparative sintered alloys 81 to 82 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 41, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 293 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 47 shown in 19 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 81 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 82 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size of 1 μm and a SUS430 (Fe-17% Cr) powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 42, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1200° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 294 of the present invention and comparative sintered alloys 83 to 84.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 294 of the present invention and the comparative sintered alloys 83 to 84 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 42, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 294 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 48 shown in 20 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 83 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 84 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size of 1 μm, a C powder having an average particle size of 18 μm and a SUS410 (Fe-13% Cr) powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 43, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1200° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 295 of the present invention and comparative sintered alloys 85 to 86.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 295 of the present invention and the comparative sintered alloys 85 to 86 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 43, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 295 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 49 shown in 21 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 85 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 86 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
As raw powders, a SrCO3 powder having an average particle size of 1 μm and a SUS630 (Fe-17% Cr-4% Ni-4% Cu-0.3% Nb) powder having an average particle size of 80 μm were prepared. These raw powders were blended according to the formulation shown in Table 44, mixed in a double corn mixer and compacted to obtain a green compact, and then the resulting green compact was sintered in a vacuum atmosphere at 0.1 Pa under the conditions of a temperature of 1200° C. and a retention time of 60 minutes to obtain an iron-based sintered alloy 296 of the present invention and comparative sintered alloys 87 to 88.
Cylindrical sintered alloy blocks for piercing test each having a diameter of 30 mm and a height of 10 mm, made of the sintered alloy 296 of the present invention and the comparative sintered alloys 87 to 88 were produced and these cylindrical sintered alloy blocks for piercing test were repeatedly pierced until the drill is damaged, using a high-speed steel drill having a diameter of 1.2 mm, under the following conditions:
As is apparent from the results shown in Table 44, the number of piercing of the cylindrical sintered alloy block for piercing test made of the sintered alloy 296 of the present invention is larger than that of the cylindrical sintered alloy block for piercing test made of the conventional sintered alloy 50 shown in 22 and therefore the sintered alloy of the present invention is excellent in machinability. However, the comparative sintered alloy 87 containing SrCO3 in the content of less than the range defined in the present invention is inferior in machinability because of small number of piercing, while the comparative sintered alloy 88 containing SrCO3 in the content of more than the range defined in the present invention is excellent in machinability because of large number of piercing, but shows drastically decreased deflection strength, and therefore it is not preferred.
The iron-based sintered alloy containing a machinability improving component comprising CaCO3 and the iron-based sintered alloy containing a machinability improving component comprising SrCO3 according to the present invention are excellent in machinability. Therefore, in various electric and machine components made of the iron-based sintered alloys of the present invention, the cost of machining such as piercing, cutting or grinding can be reduced. Thus, the present invention can contribute largely toward the development of mechanical industry by providing various machine components, which require dimensional accuracy, at low cost.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2003-062854 | Mar 2003 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2004/003094 | 3/10/2004 | WO | 00 | 9/8/2005 |
| Publishing Document | Publishing Date | Country | Kind |
|---|---|---|---|
| WO2004/081249 | 9/23/2004 | WO | A |
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| Number | Date | Country | |
|---|---|---|---|
| 20060198752 A1 | Sep 2006 | US |
