Patent Grant
10773302
The present invention relates to a metal powder for powder metallurgy, a compound, a granulated powder, and a sintered body.
In a powder metallurgy method, a composition containing a metal powder and a binder is molded into a desired shape to obtain a molded body, and the obtained molded body is degreased and sintered, whereby a sintered body is produced. In such a process for producing a sintered body, an atomic diffusion phenomenon occurs among particles of the metal powder, whereby the molded body is gradually densified, resulting in sintering.
For example, JP-A-2012-87416 (Patent Document 1) proposes a metal powder for powder metallurgy which contains Zr and Si, with the remainder including at least one element selected from the group consisting of Fe, Co, and Ni, and unavoidable elements. According to such a metal powder for powder metallurgy, the sinterability is improved by the action of Zr, whereby a sintered body having a high density can be easily produced.
Further, for example, JP-A-6-279913 (Patent Document 2) discloses a composition for metal injection molding containing 100 parts by weight of a stainless steel powder composed of C (0.03 wt % or less), Ni (8 to 32 wt %), Cr (12 to 32 wt %), and Mo (1 to 7 wt %), with the remainder including Fe and unavoidable impurities, and 0.1 to 5.5 parts by weight of at least one type of powder composed of Ti or/and Nb and having an average particle diameter of 10 to 60 μm. By using such a composition obtained by mixing two types of powders, a sintered body having a high sintered density and excellent corrosion resistance is obtained.
Further, for example, JP-A-2007-177675 (Patent Document 3) discloses a needle seal for a needle valve, which has a composition containing C (0.95 to 1.4 mass %), Si (1.0 mass % or less), Mn (1.0 mass % or less), Cr (16 to 18 mass %), and Nb (0.02 to 3 mass %), with the remainder including Fe and unavoidable impurities, has a density after sintering of 7.65 to 7.75 g/cm3, and is obtained by molding using a metal injection molding method. According to this, a needle seal having a high density is obtained.
The thus obtained sintered body is getting widely used in various machine components, structural components, etc. recently.
However, depending on the use of a sintered body, further densification is needed in some cases. In such a case, a sintered body is further subjected to an additional treatment such as a hot isostatic pressing treatment (HIP treatment) to increase the density, however, the workload is significantly increased, and also an increase in the cost is inevitable.
Therefore, an expectation for realization of a metal powder capable of producing a sintered body having a high density without performing an additional treatment or the like has increased.
An advantage of some aspects of the invention is to provide a metal powder for powder metallurgy, a compound, and a granulated powder, each of which is capable of producing a sintered body having a high density, and a sintered body which has a high density.
The advantage can be achieved by the following configurations.
A metal powder for powder metallurgy according to an aspect of the invention contains Fe as a principal component, Ni in a proportion of 5 mass % or more and 20 mass % or less, Si in a proportion of 0.3 mass % or more and 5 mass % or less, and C in a proportion of 0.005 mass % or more and 0.3 mass % or less, wherein when one element selected from the group consisting of Ti, V, Y, Zr, Nb, Hf, and Ta is defined as a first element, and one element selected from the group consisting of Ti, V, Y, Zr, Nb, Hf, and Ta, and having a higher group number in the periodic table than that of the first element or having the same group number in the periodic table as that of the first element and a higher period number in the periodic table than that of the first element is defined as a second element, the first element is contained in a proportion of 0.01 mass % or more and 0.7 mass % or less, and the second element is contained in a proportion of 0.01 mass % or more and 0.7 mass % or less.
According to this configuration, the alloy composition is optimized so that the densification during sintering of the metal powder for powder metallurgy can be enhanced. As a result, a metal powder for powder metallurgy capable of producing a sintered body having a high density is obtained without performing an additional treatment.
In the metal powder for powder metallurgy according to the aspect of the invention, it is preferred that when a ratio X1/X2 of a value X1 obtained by dividing the content E1 of the first element by the mass number of the first element to a value X2 obtained by dividing the content E2 of the second element by the mass number of the second element is 0.3 or more and 3 or less.
According to this configuration, when the metal powder for powder metallurgy is fired, a difference in timing between the deposition of a carbide or the like of the first element and the deposition of a carbide or the like of the second element can be optimized. As a result, pores remaining in a molded body can be eliminated as if they were swept out sequentially from the inside, and therefore, pores generated in the sintered body can be minimized. Accordingly, a metal powder for powder metallurgy capable of producing a sintered body having a high density and excellent mechanical properties is obtained.
In the metal powder for powder metallurgy according to the aspect of the invention, it is preferred that the sum of the content of the first element and the content of the second element is 0.05 mass % or more and 0.8 mass % or less.
According to this configuration, the densification of a sintered body to be produced becomes necessary and sufficient.
In the metal powder for powder metallurgy according to the aspect of the invention, it is preferred that Cr is further contained in a proportion of 9 mass % or more and 15 mass % or less.
According to this configuration, a metal powder for powder metallurgy capable of producing a sintered body which can maintain high mechanical properties over a long period of time is obtained.
In the metal powder for powder metallurgy according to the aspect of the invention, it is preferred that Co is further contained in a proportion of 6 mass % or more and 14 mass % or less.
According to this configuration, a metal powder for powder metallurgy capable of producing a sintered body whose heat resistance is further enhanced without causing a large decrease in the density of the sintered body to be produced is obtained.
In the metal powder for powder metallurgy according to the aspect of the invention, it is preferred that the metal powder has an average particle diameter of 0.5 μm or more and 30 μm or less.
According to this configuration, pores remaining in a sintered body are extremely decreased, and therefore, a sintered body having a particularly high density and particularly excellent mechanical properties can be produced.
A compound according to an aspect of the invention includes the metal powder for powder metallurgy according to the aspect of the invention and a binder which binds the particles of the metal powder for powder metallurgy to one another.
According to this configuration, a compound capable of producing a sintered body having a high density is obtained.
A granulated powder according to an aspect of the invention includes the metal powder for powder metallurgy according to the aspect of the invention which is granulated.
According to this configuration, a granulated powder capable of producing a sintered body having a high density is obtained.
A sintered body according to an aspect of the invention contains Fe as a principal component, Ni in a proportion of 5 mass % or more and 20 mass % or less, Si in a proportion of 0.3 mass % or more and 5 mass % or less, and C in a proportion of 0.005 mass % or more and 0.3 mass % or less, wherein when one element selected from the group consisting of Ti, V, Y, Zr, Nb, Hf, and Ta is defined as a first element, and one element selected from the group consisting of Ti, V, Y, Zr, Nb, Hf, and Ta, and having a higher group number in the periodic table than that of the first element or having the same group number in the periodic table as that of the first element and a higher period number in the periodic table than that of the first element is defined as a second element, the first element is contained in a proportion of 0.01 mass % or more and 0.7 mass % or less, and the second element is contained in a proportion of 0.01 mass % or more and 0.7 mass % or less.
According to this configuration, a sintered body having a high density is obtained without performing an additional treatment.
Hereinafter, a metal powder for powder metallurgy, a compound, a granulated powder, and a sintered body according to the invention will be described in detail.
Metal Powder for Powder Metallurgy
First, a metal powder for powder metallurgy according to the invention will be described.
In powder metallurgy, a sintered body having a desired shape can be obtained by molding a composition containing a metal powder for powder metallurgy and a binder into a desired shape, followed by degreasing and sintering. According to such a powder metallurgy technique, an advantage that a sintered body with a complicated and fine shape can be produced in a near-net shape (a shape close to a final shape) as compared with the other metallurgy techniques is obtained.
With respect to the metal powder for powder metallurgy to be used in the powder metallurgy, an attempt to increase the density of a sintered body to be produced by appropriately changing the composition thereof has been made. However, in the sintered body, pores are liable to be generated, and therefore, in order to obtain mechanical properties comparable to those of ingot materials, it was necessary to further increase the density of the sintered body.
Therefore, in the past, the obtained sintered body was further subjected to an additional treatment such as a hot isostatic pressing treatment (HIP treatment) to increase the density in some cases. However, such an additional treatment requires much time, labor, and cost, and therefore becomes an obstacle to the expansion of the application of the sintered body.
In consideration of the above-mentioned problems, the present inventors have made intensive studies to find conditions for obtaining a sintered body having a high density without performing an additional treatment. As a result, they found that the density of a sintered body can be increased by optimizing the composition of an alloy which forms a metal powder, and thus completed the invention.
Specifically, the metal powder for powder metallurgy according to the invention is a metal powder which contains Fe as a principal component, Ni in a proportion of 5 mass % or more and 20 mass % or less, Si in a proportion of 0.3 mass % or more and 5 mass % or less, and C in a proportion of 0.005 mass % or more and 0.3 mass % or less, and in which when one element selected from the group consisting of Ti, V, Y, Zr, Nb, Hf, and Ta is defined as a first element, and one element selected from the group consisting of Ti, V, Y, Zr, Nb, Hf, and Ta, and having a higher group number in the periodic table than that of the first element or having the same group number in the periodic table as that of the first element and a higher period number in the periodic table than that of the first element is defined as a second element, the first element is contained in a proportion of 0.01 mass % or more and 0.7 mass % or less, and the second element is contained in a proportion of 0.01 mass % or more and 0.7 mass % or less. According to such a metal powder, as a result of optimizing the alloy composition, the densification during sintering can be particularly enhanced. As a result, a sintered body having a high density can be produced without performing an additional treatment.
By increasing the density of a sintered body, a sintered body having excellent mechanical properties is obtained. Such a sintered body can be widely applied also to, for example, machine components, structural components, and the like, to which an external force (load) is applied.
The first element is one element selected from the group consisting of the following seven elements: Ti, V, Y, Zr, Nb, Hf, and Ta, and the second element is one element selected from the group consisting of the above-mentioned seven elements and having a higher group number in the periodic table than that of the first element or one element selected from the group consisting of the above-mentioned seven elements and having the same group number in the periodic table as that of the element selected as the first element and a higher period number in the periodic table than that of the first element.
Hereinafter, the alloy composition of the metal powder for powder metallurgy according to the invention will be described in further detail. In the following description, the “metal powder for powder metallurgy” is sometimes simply referred to as “metal powder”.
Ni
Ni is an element which imparts corrosion resistance and heat resistance to a sintered body to be produced.
The content of Ni in the metal powder is set to 5 mass % or more and 20 mass % or less, but is set to preferably 5.5 mass % or more and 19.5 mass % or less, more preferably 6 mass % or more and 19 mass % or less. By setting the content of Ni within the above range, a sintered body having excellent mechanical properties over a long period of time is obtained.
When the content of Ni is less than the above lower limit, the corrosion resistance or heat resistance of a sintered body to be produced may not be sufficiently increased depending on the overall composition, and on the other hand, when the content of Ni exceeds the above upper limit, the corrosion resistance or heat resistance may be decreased instead.
A particularly preferred range of the content of Ni is appropriately set according to the contents of the below-mentioned Si and Cr.
For example, in the case where the content of Si in the metal powder is less than 3 mass % and the content of Cr therein is less than 13 mass %, the content of Ni is preferably 16 mass % or more and 20 mass % or less, more preferably 17 mass % or more and 19 mass % or less.
Further, in the case where the content of Si in the metal powder is 3 mass % or more, the content of Ni is preferably 5 mass % or more and 8 mass % or less, more preferably 6 mass % or more and 7 mass % or less.
Si
Si (silicon) is an element which imparts corrosion resistance and high mechanical properties to a sintered body to be produced, and by using the metal powder containing Si, a sintered body capable of maintaining high mechanical properties over a long period of time is obtained.
The content of Si in the metal powder is set to 0.3 mass % or more and 5 mass % or less, but is set to preferably 0.4 mass % or more and 4.5 mass % or less, more preferably 0.5 mass % or more and 4 mass % or less. When the content of Si is less than the above lower limit, the effect of the addition of Si is weakened depending on the overall composition, and therefore, the corrosion resistance or mechanical properties of a sintered body to be produced is/are deteriorated. On the other hand, when the content of Si exceeds the above upper limit, the amount of Si is too large depending on the overall composition, and therefore, the corrosion resistance or mechanical properties is/are decreased instead.
C
C (carbon) can particularly enhance the sinterability when it is used in combination with the below-mentioned first element and second element. Specifically, the first element and the second element each form a carbide by binding to C. By dispersedly depositing this carbide, an effect of preventing the significant growth of crystal grains is exhibited. A clear reason for obtaining such an effect is not known, but one of the reasons is considered to be because the dispersed deposit serves as an obstacle to inhibit the significant growth of crystal grains, and therefore, a variation in the size of crystal grains is suppressed. Accordingly, it becomes difficult to generate pores in a sintered body, and also the increase in the size of crystal grains is prevented, and thus, a sintered body having a high density and excellent mechanical properties is obtained.
The content of C in the metal powder is set to 0.005 mass % or more and 0.3 mass % or less, but is set to preferably 0.008 mass % or more and 0.15 mass % or less, more preferably 0.01 mass % or more and 0.08 mass % or less. When the content of C is less than the above lower limit, crystal grains are liable to grow depending on the overall composition, and therefore, the mechanical properties of the sintered body become insufficient. On the other hand, when the content of C exceeds the above upper limit, the amount of C is too large depending on the overall composition, and therefore, the sinterability is decreased instead.
Al
The metal powder for powder metallurgy according to the invention may contain either one of Al (aluminum) and Cu (copper), and may contain both.
Al is an element which deposits an intermetallic compound in a sintered body to be produced and enhances the mechanical properties of the sintered body. Further, in the case where Cu is contained in the metal powder, further, Al may be contained therein.
The content of Al in the metal powder is not particularly limited, but is preferably 0.03 mass % or more and 5 mass % or less, more preferably 0.04 mass % or more and 3 mass % or less, further more preferably 0.75 mass % or more and 2 mass % or less. By setting the content of Al within the above range, the mechanical properties of a sintered body to be produced can be further enhanced without causing a large decrease in the density of the sintered body.
When the content of Al is less than the above lower limit, the deposition of an intermetallic compound is limited, and therefore, the mechanical properties of the sintered body may not be able to be sufficiently enhanced. On the other hand, when the content of Al exceeds the above upper limit, an intermetallic compound may be excessively deposited, and therefore, the density of the sintered body may be decreased, and also the mechanical properties of the sintered body may be decreased instead.
Cu
Cu is an element which deposits an intermetallic compound in a sintered body to be produced and enhances the mechanical properties of the sintered body. Further, in the case where Al is contained in the metal powder, further, Cu may be contained therein.
The content of Cu in the metal powder is not particularly limited, but is preferably 0.03 mass % or more and 5 mass % or less, more preferably 0.04 mass % or more and 4.5 mass % or less, further more preferably 0.75 mass % or more and 4.2 mass % or less. By setting the content of Cu within the above range, the mechanical properties of a sintered body to be produced can be further enhanced without causing a large decrease in the density of the sintered body.
When the content of Cu is less than the above lower limit, the deposition of an intermetallic compound is limited, and therefore, the mechanical properties of the sintered body may not be able to be sufficiently enhanced. On the other hand, when the content of Cu exceeds the above upper limit, an intermetallic compound may be excessively deposited, and therefore, the density of the sintered body may be decreased, and also the mechanical properties of the sintered body may be decreased instead.
Cr
The metal powder for powder metallurgy according to the invention may contain Cr (chromium).
Cr is an element which imparts corrosion resistance to a sintered body to be produced, and by using the metal powder containing Cr, a sintered body capable of maintaining high mechanical properties over a long period of time is obtained.
The content of Cr in the metal powder is not particularly limited, but is set to 9 mass % or more and 15 mass % or less, but is set to preferably 9.5 mass % or more and 14 mass % or less, more preferably 10 mass % or more and 13 mass % or less. By setting the content of Cr within the above range, a metal powder capable of producing a sintered body which can maintain high mechanical properties over a long period of time is obtained. When the content of Cr is less than the above lower limit, the corrosion resistance of a sintered body to be produced may be insufficient depending on the overall composition. On the other hand, when the content of Cr exceeds the above upper limit, the sinterability may be deteriorated depending on the overall composition, and therefore, it may become difficult to increase the density of the sintered body.
A particularly preferred range of the content of Cr is appropriately set according to the content of the below-mentioned Al and Cu.
For example, in the case where Al is contained in a proportion of 0.03 mass % or more and 5 mass % or less in the metal powder, the content of Cr is particularly preferably less than 9 mass %.
On the other hand, in the case where Cu is contained in a proportion of 0.03 mass % or more and 5 mass % or less in the metal powder, the content of Cr is particularly preferably 9 mass % or more and 15 mass % or less.
Co
The metal powder for powder metallurgy may contain Co (cobalt).
Co is an element which enhances the heat resistance of a sintered body to be produced.
The content of Co in the metal powder is not particularly limited, but is preferably 6 mass % or more and 14 mass % or less, more preferably 7 mass % or more and 13 mass % or less, further more preferably 7.5 mass % or more and 12.5 mass % or less. By setting the content of Co within the above range, the heat resistance of a sintered body to be produced can be further enhanced without causing a large decrease in the density of the sintered body.
Particularly preferred ranges of the content of Co and the content of the above-mentioned Cr are appropriately set according to the content of the above-mentioned Ni.
For example, in the case where the content of Ni in the metal powder is 10 mass % or more, Co is preferably contained within the above range, and with respect to Cr, the content thereof is preferably comparable to or less than the content of the below-mentioned impurities.
On the other hand, in the case where the content of Ni in the metal powder is less than 10 mass %, Cr is preferably contained within the above range, and with respect to Co, the content thereof is preferably comparable to or less than the content of the below-mentioned impurities.
Mo
The metal powder for powder metallurgy may contain Mo (molybdenum).
Mo is an element which enhances the corrosion resistance of a sintered body to be produced.
The content of Mo in the metal powder is not particularly limited, but is preferably 0.1 mass % or more and 6 mass % or less, more preferably 0.3 mass % or more and 5.2 mass % or less, further more preferably 0.5 mass % or more and 5 mass % or less. By setting the content of Mo within the above range, the corrosion resistance of a sintered body to be produced can be further enhanced without causing a large decrease in the density of the sintered body.
First Element and Second Element
The first element and the second element each deposit a carbide or an oxide (hereinafter also collectively referred to as “carbide or the like”). It is considered that this deposited carbide or the like inhibits the significant growth of crystal grains when the metal powder is sintered. As a result, as described above, it becomes difficult to generate pores in a sintered body, and also the increase in the size of crystal grains is prevented, and thus, a sintered body having a high density and excellent mechanical properties is obtained.
In addition, although a detailed description will be given later, the deposited carbide or the like promotes the accumulation of silicon oxide at a crystal grain boundary, and as a result, the sintering is promoted and the density is increased while preventing the increase in the size of crystal grains.
The first element and the second element are two elements selected from the group consisting of the following seven elements: Ti, V, Y, Zr, Nb, Hf, and Ta, but preferably include an element belonging to group IIIA or group IVA in the long periodic table (Ti, Y, Zr, or Hf). By including an element belonging to group IIIA or group IVA as at least one of the first element and the second element, oxygen contained as an oxide in the metal powder is removed and the sinterability of the metal powder can be particularly enhanced.
The first element is only required to be one element selected from the group consisting of the following seven elements: Ti, V, Y, Zr, Nb, Hf, and Ta as described above, but is preferably an element belonging to group IIIA or group IVA in the long periodic table in the group consisting of the above-mentioned seven elements. An element belonging to group IIIA or group IVA removes oxygen contained as an oxide in the metal powder and therefore can particularly enhance the sinterability of the metal powder. According to this, the concentration of oxygen remaining in the crystal grains after sintering can be decreased. As a result, the content of oxygen in the sintered body can be decreased, and the density can be increased. Further, these elements are elements having high activity, and therefore are considered to cause rapid atomic diffusion. Accordingly, this atomic diffusion acts as a driving force, and thereby a distance between particles of the metal powder is efficiently decreased and a neck is formed between the particles, so that the densification of a molded body is promoted. As a result, the density of the sintered body can be further increased.
On the other hand, the second element is only required to be one element selected from the group consisting of the following seven elements: Ti, V, Y, Zr, Nb, Hf, and Ta and different from the first element as described above, but is preferably an element belonging to group VA in the long periodic table in the group consisting of the above-mentioned seven elements. An element belonging to group VA particularly efficiently deposits the above-mentioned carbide or the like, and therefore, can efficiently inhibit the significant growth of crystal grains during sintering. As a result, the formation of fine crystal grains is promoted, and thus, the density of the sintered body can be increased and also the mechanical properties of the sintered body can be enhanced.
Incidentally, by the combination of the first element with the second element composed of the elements as described above, the effects of the respective elements are exhibited without inhibiting each other. Due to this, the metal powder containing such a first element and a second element enables the production of a sintered body having a particularly high density.
More preferably, a combination of an element belonging to group IVA as the first element with Nb as the second element is adopted.
Further, more preferably, a combination of Zr or Hf as the first element with Nb as the second element is adopted.
By adopting such a combination, the above-mentioned effect becomes more prominent.
Among these elements, Zr is a ferrite forming element, and therefore deposits a body-centered cubic lattice phase. This body-centered cubic lattice phase has more excellent sinterability than the other crystal lattice phases, and therefore contributes to the densification of a sintered body.
The content of the first element in the metal powder is set to 0.01 mass % or more and 0.7 mass % or less, but is set to preferably 0.03 mass % or more and 0.65 mass % or less, more preferably 0.05 mass % or more and 0.6 mass % or less. When the content of the first element is less than the above lower limit, the effect of the addition of the first element is weakened depending on the overall composition, and therefore, the density of a sintered body to be produced is not sufficiently increased. On the other hand, when the content of the first element exceeds the above upper limit, the amount of the first element is too large depending on the overall composition, and therefore, the ratio of the above-mentioned carbide or the like is too high, and the densification is deteriorated instead.
The content of the second element in the metal powder is set to 0.01 mass % or more and 0.7 mass % or less, but is set to preferably 0.03 mass % or more and 0.55 mass % or less, more preferably 0.05 mass % or more and 0.45 mass % or less. When the content of the second element is less than the above lower limit, the effect of the addition of the second element is weakened depending on the overall composition, and therefore, the density of a sintered body to be produced is not sufficiently increased. On the other hand, when the content of the second element exceeds the above upper limit, the amount of the second element is too large depending on the overall composition, and therefore, the ratio of the above-mentioned carbide or the like is too high, and the densification is deteriorated instead.
Further, as described above, each of the first element and the second element deposits a carbide or the like, however, in the case where an element belonging to group IIIA or group IVA is selected as the first element as described above and an element belonging to group VA is selected as the second element as described above, it is presumed that when the metal powder is sintered, the timing when a carbide or the like of the first element is deposited and the timing when a carbide or the like of the second element is deposited differ from each other. It is considered that due to the difference in timing when a carbide or the like is deposited in this manner, sintering gradually proceeds so that the generation of pores is prevented, and thus, a dense sintered body is obtained. That is, it is considered that by the presence of both of the carbide or the like of the first element and the carbide or the like of the second element, the increase in the size of crystal grains can be suppressed while increasing the density of the sintered body.
In the metal powder, it is only necessary that two elements selected from the group consisting of the above-mentioned seven elements are contained, however, an element which is selected from this group and is different from the two elements may be further contained. That is, in the metal powder, three or more elements selected from the group consisting of the above-mentioned seven elements may be contained. According to this, although it varies a little depending on the combination of the elements, the above-mentioned effect can be further enhanced.
Further, it is preferred to set the ratio of the content of the first element to the content of the second element in consideration of the mass number of the element selected as the first element and the mass number of the element selected as the second element.
Specifically, when a value obtained by dividing the content E1 (mass %) of the first element by the mass number of the first element is represented by an index X1 and a value obtained by dividing the content E2 (mass %) of the second element by the mass number of the second element is represented by an index X2, the ratio (X1/X2) of the index X1 to the index X2 is preferably 0.3 or more and 3 or less, more preferably 0.5 or more and 2 or less, further more preferably 0.75 or more and 1.3 or less. By setting the ratio X1/X2 within the above range, when the metal powder is fired, a difference between the timing when a carbide or the like of the first element is deposited and the timing when a carbide or the like of the second element is deposited can be optimized. According to this, pores remaining in a molded body can be eliminated as if they were swept out sequentially from the inside, and therefore, pores generated in a sintered body can be minimized. Therefore, by setting the ratio X1/X2 within the above range, a metal powder capable of producing a sintered body having a high density and excellent mechanical properties can be obtained. Further, the balance between the number of atoms of the first element and the number of atoms of the second element is optimized, and therefore, an effect brought about by the first element and an effect brought about by the second element are synergistically exhibited, and thus, a sintered body having a particularly high density can be obtained.
Here, with respect to a specific example of the combination of the first element with the second element, based on the above-mentioned range of the ratio X1/X2, the ratio E1/E2 of the content E1 (mass %) to the content E2 (mass %) is also calculated.
For example, in the case where the first element is Zr and the second element is Nb, since the mass number of Zr is 91.2 and the mass number of Nb is 92.9, E1/E2 is preferably 0.29 or more and 2.95 or less, more preferably 0.49 or more and 1.96 or less.
In the case where the first element is Hf and the second element is Nb, since the mass number of Hf is 178.5 and the mass number of Nb is 92.9, E1/E2 is preferably 0.58 or more and 5.76 or less, more preferably 0.96 or more and 3.84 or less.
In the case where the first element is Ti and the second element is Nb, since the mass number of Ti is 47.9 and the mass number of Nb is 92.9, E1/E2 is preferably 0.15 or more and 1.55 or less, more preferably 0.26 or more and 1.03 or less.
In the case where the first element is Nb and the second element is Ta, since the mass number of Nb is 92.9 and the mass number of Ta is 180.9, E1/E2 is preferably 0.15 or more and 1.54 or less, more preferably 0.26 or more and 1.03 or less.
In the case where the first element is Y and the second element is Nb, since the mass number of Y is 88.9 and the mass number of Nb is 92.9, E1/E2 is preferably 0.29 or more and 2.87 or less, more preferably 0.48 or more and 1.91 or less.
In the case where the first element is V and the second element is Nb, since the mass number of V is 50.9 and the mass number of Nb is 92.9, E1/E2 is preferably 0.16 or more and 1.64 or less, more preferably 0.27 or more and 1.10 or less.
In the case where the first element is Ti and the second element is Zr, since the mass number of Ti is 47.9 and the mass number of Zr is 91.2, E1/E2 is preferably 0.16 or more and 1.58 or less, more preferably 0.26 or more and 1.05 or less.
In the case where the first element is Zr and the second element is Ta, since the mass number of Zr is 91.2 and the mass number of Ta is 180.9, E1/E2 is preferably 0.15 or more and 1.51 or less, more preferably 0.25 or more and 1.01 or less.
In the case where the first element is Zr and the second element is V, since the mass number of Zr is 91.2 and the mass number of V is 50.9, E1/E2 is preferably 0.54 or more and 5.38 or less, more preferably 0.90 or more and 3.58 or less.
Also in the case of a combination other than the above-mentioned combinations, E1/E2 can be calculated in the same manner as described above.
The sum (E1+E2) of the content E1 of the first element and the content E2 of the second element is preferably 0.05 mass % or more and 0.8 mass % or less, more preferably 0.10 mass % or more and 0.7 mass % or less, further more preferably 0.12 mass % or more and 0.6 mass % or less. By setting the sum of the content of the first element and the content of the second element within the above range, the densification of a sintered body to be produced becomes necessary and sufficient.
When the ratio of the sum of the content of the first element and the content of the second element to the content of Si is represented by (E1+E2)/Si, (E1+E2)/Si is preferably 0.01 or more and 0.7 or less, more preferably 0.015 or more and 0.6 or less, further more preferably 0.02 or more and 0.5 or less. By setting the ratio (E1+E2)/Si within the above range, a decrease in the toughness or the like when Si is added is sufficiently compensated by the addition of the first element and the second element. As a result, a metal powder capable of producing a sintered body which has excellent mechanical properties such as toughness in spite of having a high density and also has excellent corrosion resistance attributed to Si is obtained.
In addition, it is considered that by the addition of appropriate amounts of the first element and the second element, the carbide or the like of the first element and the carbide or the like of the second element act as “nuclei”, and silicon oxide is accumulated at a crystal grain boundary in the sintered body. By the accumulation of silicon oxide at a crystal grain boundary, the concentration of oxides inside the crystal grain is decreased, and therefore, sintering is promoted. As a result, it is considered that the densification of the sintered body is further promoted.
The deposited silicon oxide easily moves to the triple point of a crystal grain boundary during the accumulation, and therefore, the crystal growth is suppressed at this point (a flux pinning effect). As a result, the significant growth of crystal grains is suppressed, and thus, a sintered body having finer crystals is obtained. Such a sintered body has particularly high mechanical properties.
The accumulated silicon oxide is easily located at the triple point of a crystal grain boundary as described above, and therefore tends to be formed into a granular shape. Therefore, in the sintered body, a first region which is in such a granular shape and has a relatively high silicon oxide content and a second region which has a relatively lower silicon oxide content than the first region are likely to be formed. By the presence of the first region, the concentration of oxides inside the crystal is decreased, and the significant growth of crystal grains is suppressed as described above.
When a qualitative and quantitative analysis is performed for the first region and the second region using an electron beam microanalyzer (EPMA), the first region contains (oxygen) as a principal element, and the second region contains Fe as a principal element. As described above, the first region mainly exists at a crystal grain boundary, and the second region exists mainly inside the crystal grain. Therefore, in the first region, when the sum of the contents of the two elements, O and Si, and the content of Fe are compared, the sum of the contents of the two elements is higher than the content of Fe. On the other hand, in the second region, the sum of the contents of the two elements, O and Si, is much smaller than the content of Fe. Based on these analysis results, it is found that Si and O are accumulated in the first region. Specifically, the sum of the content of Si and the content of O is preferably 1.5 times or more and 10000 times or less the content of Fe in the first region. Further, the content of Si in the first region is preferably 3 times or more and 10000 times or less the content of Si in the second region.
Further, at least one of the content of the first element and the content of the second element often satisfies the relationship that the content in the first region is higher than the content in the second region, which varies depending on the compositional ratio in some cases. This indicates that in the first region, the carbide or the like of the first element and the carbide or the like of the second element act as nuclei when silicon oxide is accumulated. Specifically, the content of the first element in the first region is preferably 3 times or more and 10000 times or less the content of the first element in the second region. Similarly, the content of the second element in the first region is preferably 3 times or more and 10000 times or less the content of the second element in the second region.
The accumulation of silicon oxide as described above is considered to be one of the causes for the densification of a sintered body. Therefore, it is considered that even in a sintered body having a density increased according to the invention, silicon oxide is not accumulated depending on the compositional ratio in some cases. That is, the first region and the second region may not be included depending on the compositional ratio.
The diameter of the first region in a granular shape varies depending on the content of Si in the entire sintered body, but is set to about 0.5 μm or more and 15 μm or less, and preferably about 1 μm or more and 10 μm or less. According to this, the densification of the sintered body can be sufficiently promoted while preventing the decrease in the mechanical properties of the sintered body accompanying the accumulation of silicon oxide.
The diameter of the first region can be obtained as the average of the diameter of a circle having the same area (circle equivalent diameter) as that of the first region determined by the color density in an electron micrograph of the cross section of the sintered body. When the average is obtained, the measured values of 10 or more regions are used.
Further, when the ratio of the sum of the content of the first element and the content of the second element to the content of C is represented by (E1+E2)/C, (E1+E2)/C is preferably 1 or more and 16 or less, more preferably 2 or more and 13 or less, further more preferably 3 or more and 10 or less. By setting the ratio (E1+E2)/C within the above range, an increase in the hardness and a decrease in the toughness when C is added, and an increase in the density brought about by the addition of the first element and the second element can be both achieved. As a result, a metal powder capable of producing a sintered body which has excellent mechanical properties such as tensile strength and toughness is obtained.
Other Elements
The metal powder for powder metallurgy according to the invention may contain, other than the above-mentioned elements, at least one element of Mn, W, N, and S as needed. These elements are also inevitably contained in some cases.
Mn is an element which imparts corrosion resistance and high mechanical properties to a sintered body to be produced in the same manner as Si.
The content of Mn in the metal powder is not particularly limited, but is preferably 0.05 mass % or more and 1.5 mass % or less, more preferably 0.1 mass % or more and 1 mass % or less. By setting the content of Mn within the above range, a sintered body having a high density and excellent mechanical properties is obtained. Further, Mn can increase the mechanical strength while suppressing the decrease in elongation. Further, Mn can suppress the increase in brittleness at a high temperature (when glowing).
If the content of Mn is less than the above lower limit, the corrosion resistance and the mechanical properties of a sintered body to be produced may not be sufficiently enhanced depending on the overall composition. On the other hand, if the content of Mn exceeds the above upper limit, the corrosion resistance or the mechanical properties may be decreased instead.
W is an element which enhances the heat resistance of a sintered body to be produced.
The content of W in the metal powder is not particularly limited, but is preferably 1 mass % or more and 4 mass % or less, more preferably 2 mass % or more and 3 mass % or less. By setting the content of W within the above range, the heat resistance of a sintered body to be produced can be further enhanced without causing a large decrease in the density of the sintered body.
N is an element which enhances the mechanical properties such as proof stress of a sintered body to be produced.
The content of N in the metal powder is not particularly limited, but is preferably 0.03 mass % or more and 1 mass % or less, more preferably 0.08 mass % or more and 0.5 mass % or less, further more preferably 0.1 mass % or more and 0.3 mass % or less. By setting the content of N within the above range, the mechanical properties such as proof stress of a sintered body to be produced can be further enhanced without causing a large decrease in the density of the sintered body.
In the case where the metal powder to which N is added is produced, for example, a method in which a nitrided raw material is used, a method in which nitrogen gas is introduced into a molten metal, a method in which the produced metal powder is subjected to a nitriding treatment, or the like is used.
S is an element which enhances the machinability of a sintered body to be produced.
The content of S in the metal powder is not particularly limited, but is preferably 0.5 mass % or less, more preferably 0.01 mass % or more and 0.3 mass % or less. By setting the content of S within the above range, the machinability of a sintered body to be produced can be further enhanced without causing a large decrease in the density of the sintered body.
To the metal powder for powder metallurgy according to the invention, B, Se, Te, Pd, or the like may be added other than the above-mentioned elements. At this time, the contents of these elements are not particularly limited, but the content of each of these elements is preferably less than 0.1 mass %, and even the total content of these elements is preferably less than 0.2 mass %. These elements are also inevitably contained in some cases.
The metal powder for powder metallurgy according to the invention may contain impurities. Examples of the impurities include all elements other than the above-mentioned elements, and specific examples thereof include Li, Be, Na, Mg, P, K, Ca, Sc, Zn, Ga, Ge, Ag, In, Sn, Sb, Os, Ir, Pt, Au, and Bi. The incorporation amounts of these impurity elements are preferably set such that the content of each of the impurity elements is less than the content of each of Fe, Ni, Si, C, the first element, and the second element. Further, the incorporation amounts of these impurity elements are preferably set such that the content of each of the impurity elements is less than 0.03 mass %, more preferably less than 0.02 mass %. Further, even the total content of these impurity elements is set to preferably less than 0.3 mass %, more preferably less than 0.2 mass %. These elements do not inhibit the effect as described above as long as the contents thereof are within the above range, and therefore may be intentionally added to the metal powder.
Meanwhile, O (oxygen) may also be intentionally added to or inevitably mixed in the metal powder, however, the amount thereof is preferably about 0.8 mass % or less, more preferably about 0.5 mass % or less. By controlling the amount of oxygen in the metal powder within the above range, the sinterability is enhanced, and thus, a sintered body having a high density and excellent mechanical properties is obtained. Incidentally, the lower limit thereof is not particularly set, but is preferably 0.03 mass % or more from the viewpoint of ease of mass production or the like.
Fe is a component (principal component) whose content is the highest in the alloy constituting the metal powder for powder metallurgy according to the invention and has a great influence on the properties of the sintered body. The content of Fe is not particularly limited, but is preferably 50 mass % or more.
The compositional ratio of the metal powder for powder metallurgy can be determined by, for example, Iron and steel—Atomic absorption spectrometric method specified in JIS G 1257 (2000), Iron and steel—ICP atomic emission spectrometric method specified in JIS G 1258 (2007), Iron and steel—Method for spark discharge atomic emission spectrometric analysis specified in JIS G 1253 (2002), Iron and steel—Method for X-ray fluorescence spectrometric analysis specified in JIS G 1256 (1997), gravimetric, titrimetric, and absorption spectrometric methods specified in JIS G 1211 to G 1237, or the like. Specifically, for example, an optical emission spectrometer for solids (spark optical emission spectrometer, model: SPECTROLAB, type: LAVMB08A) manufactured by SPECTRO Analytical Instruments GmbH or an ICP device (model: CIROS-120) manufactured by Rigaku Corporation can be used.
Incidentally, the methods specified in JIS G 1211 to G 1237 are as follows.
JIS G 1211 (2011): Iron and steel—Methods for determination of carbon content
JIS G 1212 (1997): Iron and steel—Methods for determination of silicon content
JIS G 1213 (2001): Iron and steel—Methods for determination of manganese content
JIS G 1214 (1998): Iron and steel—Methods for determination of phosphorus content
JIS G 1215 (2010): Iron and steel—Methods for determination of sulfur content
JIS G 1216 (1997): Iron and steel—Methods for determination of nickel content
JIS G 1217 (2005): Iron and steel—Methods for determination of chromium content
JIS G 1218 (1999): Iron and steel—Methods for determination of molybdenum content
JIS G 1219 (1997): Iron and steel—Methods for determination of copper content
JIS G 1220 (1994): Iron and steel—Methods for determination of tungsten content
JIS G 1221 (1998): Iron and steel—Methods for determination of vanadium content
JIS G 1222 (1999): Iron and steel—Methods for determination of cobalt content
JIS G 1223 (1997): Iron and steel—Methods for determination of titanium content
JIS G 1224 (2001): Iron and steel—Methods for determination of aluminum content
JIS G 1225 (2006): Iron and steel—Methods for determination of arsenic content
JIS G 1226 (1994): Iron and steel—Methods for determination of tin content
JIS G 1227 (1999): Iron and steel—Methods for determination of boron content
JIS G 1228 (2006): Iron and steel—Methods for determination of nitrogen content
JIS G 1229 (1994): Steel—Methods for determination of lead content
JIS G 1232 (1980): Methods for determination of zirconium in steel
JIS G 1233 (1994): Steel—Method for determination of selenium content
JIS G 1234 (1981): Methods for determination of tellurium in steel
JIS G 1235 (1981): Methods for determination of antimony in iron and steel
JIS G 1236 (1992): Method for determination of tantalum in steel
JIS G 1237 (1997): Iron and steel—Methods for determination of niobium content
Further, when C (carbon) and S (sulfur) are determined, particularly, an infrared absorption method after combustion in a current of oxygen (after combustion in a high-frequency induction heating furnace) specified in JIS G 1211 (2011) is also used. Specifically, a carbon-sulfur analyzer, CS-200 manufactured by LECO Corporation can be used.
Further, when N (nitrogen) and O (oxygen) are determined, particularly, a method for determination of nitrogen content in iron and steel specified in JIS G 1228 (2006) and a method for determination of oxygen content in metallic materials specified in JIS Z 2613 (2006) are also used. Specifically, an oxygen-nitrogen analyzer, TC-300/EF-300 manufactured by LECO Corporation can be used.
Further, the metal powder for powder metallurgy according to the invention preferably has a martensite crystal structure. The martensite crystal structure includes a body-centered cubic lattice in the form of a solid solution supersaturated with C. This body-centered cubic lattice is formed by transformation from a face-centered cubic lattice accompanying firing or a heat treatment after firing, and the volume thereof is expanded at that time. Therefore, a metal powder for powder metallurgy having a martensite crystal structure is capable of producing a sintered body having a high hardness.
It can be determined whether or not the metal powder for powder metallurgy has a martensite crystal structure by, for example, X-ray diffractometry.
The average particle diameter of the metal powder for powder metallurgy according to the invention is preferably 0.5 μm or more and 30 μm or less, more preferably 1 μm or more and 20 μm or less, further more preferably 2 μm or more and 10 μm or less. By using the metal powder for powder metallurgy having such a particle diameter, pores remaining in a sintered body are extremely reduced, and therefore, a sintered body having a particularly high density and particularly excellent mechanical properties can be produced.
The average particle diameter can be obtained as a particle diameter when the cumulative amount from the small diameter side reaches 50% in a cumulative particle size distribution on a mass basis obtained by laser diffractometry.
If the average particle diameter of the metal powder for powder metallurgy is less than the above lower limit, the moldability is deteriorated when molding the shape which is difficult to mold, and therefore, the sintered density may be decreased. On the other hand, if the average particle diameter of the metal powder exceeds the above upper limit, spaces between the particles become larger during molding, and therefore, the sintered density may be decreased also in this case.
The particle size distribution of the metal powder for powder metallurgy is preferably as narrow as possible. Specifically, when the average particle diameter of the metal powder for powder metallurgy is within the above range, the maximum particle diameter of the metal powder is preferably 200 μm or less, more preferably 150 μm or less. By controlling the maximum particle diameter of the metal powder for powder metallurgy within the above range, the particle size distribution of the metal powder for powder metallurgy can be narrowed, and thus, the density of the sintered body can be further increased.
Here, the “maximum particle diameter” refers to a particle diameter when the cumulative amount from the small diameter side reaches 99.9% in a cumulative particle size distribution on a mass basis obtained by laser diffractometry.
When the minor axis of each particle of the metal powder for powder metallurgy is represented by S (μm) and the major axis thereof is represented by L (μm), the average of the aspect ratio defined by S/L is preferably about 0.4 or more and 1 or less, more preferably about 0.7 or more and 1 or less. The metal powder for powder metallurgy having an aspect ratio within this range has a shape relatively close to a spherical shape, and therefore, the packing factor when the metal powder is molded is increased. As a result, the density of the sintered body can be further increased.
Here, the “major axis” is the maximum possible length in the projected image of the particle, and the “minor axis” is the maximum possible length in the direction perpendicular to the major axis. Incidentally, the average of the aspect ratio can be obtained as the average of the measured aspect ratios of 100 or more particles.
The tap density of the metal powder for powder metallurgy according to the invention is preferably 3.5 g/cm3 or more, more preferably 4 g/cm3 or more. According to the metal powder for powder metallurgy having such a high tap density, when a molded body is obtained, the interparticle packing efficiency is particularly increased. Therefore, a particularly dense sintered body can be obtained in the end.
The specific surface area of the metal powder for powder metallurgy according to the invention is not particularly limited, but is preferably 0.1 m2/g or more, more preferably 0.2 m2/g or more. According to the metal powder for powder metallurgy having such a large specific surface area, a surface activity (surface energy) is increased so that it is possible to easily sinter the metal powder even if less energy is applied. Therefore, when a molded body is sintered, a difference in sintering rate hardly occurs between the inner side and the outer side of the molded body, and thus, the decrease in the sintered density due to the pores remaining inside the molded body can be suppressed.
The metal powder for powder metallurgy according to the invention may be a powder (pre-alloy powder) composed only of particles having a single composition, but may also be a mixed powder (pre-mix powder) obtained by mixing a plurality of types of particles having mutually different compositions. In the case of a pre-mix powder, it is only necessary to satisfy the compositional ratio as described above as a whole. According to this, the pre-mix powder brings about the same effect as described above and enables the production of a sintered body having a high density.
Specific examples of the pre-mix powder include a mixed powder of a C powder (carbon powder) and a powder in which C (carbon) is reduced from the above-mentioned compositional ratio, and a mixed powder of a first element powder, a second element powder, and a powder in which the first element and the second element are reduced from the above-mentioned compositional ratio. The combination of a plurality of types of powders in the mixed powder is not particularly limited, and any combination may be adopted.
Method for Producing Sintered Body
Next, a method for producing a sintered body using such a metal powder for powder metallurgy according to the invention will be described.
The method for producing a sintered body includes (A) a composition preparation step in which a composition for producing a sintered body is prepared, (B) a molding step in which a molded body is produced, (C) a degreasing step in which a degreasing treatment is performed, and (D) a firing step in which firing is performed. Hereinafter, the respective steps will be described sequentially.
(A) Composition Preparation Step
First, the metal powder for powder metallurgy according to the invention and a binder are prepared, and these materials are kneaded using a kneader, whereby a kneaded material (compound) is obtained. That is, this kneaded material contains the metal powder for powder metallurgy and the binder which binds the particles of the metal powder to one another. By doing this, a kneaded material capable of producing a sintered body having a high density is obtained.
In this kneaded material (an embodiment of the compound according to the invention), the metal powder for powder metallurgy is uniformly dispersed.
The metal powder for powder metallurgy according to the invention is produced by, for example, any of a variety of powdering methods such as an atomization method (such as a water atomization method, a gas atomization method, or a spinning water atomization method), a reducing method, a carbonyl method, and a pulverization method.
Among these, the metal powder for powder metallurgy according to the invention is preferably a metal powder produced by an atomization method, more preferably a metal powder produced by a water atomization method or a spinning water atomization method. The atomization method is a method in which a molten metal (metal melt) is caused to collide with a fluid (liquid or gas) sprayed at a high speed to atomize the metal melt into a fine powder and also to cool the fine powder, whereby a metal powder is produced. By producing the metal powder for powder metallurgy through such an atomization method, an extremely fine powder can be efficiently produced. Further, the shape of the particle of the obtained powder is closer to a spherical shape by the action of surface tension. Due to this, a metal powder having a high packing factor when molding is obtained. That is, a powder capable of producing a sintered body having a high density can be obtained.
The thus obtained metal powder for powder metallurgy may be classified as needed. Examples of the classification method include dry classification such as sieving classification, inertial classification, and centrifugal classification, and wet classification such as sedimentation classification.
Examples of the binder include polyolefins such as polyethylene, polypropylene, and ethylene-vinyl acetate copolymers, acrylic resins such as polymethyl methacrylate and polybutyl methacrylate, styrenic resins such as polystyrene, polyesters such as polyvinyl chloride, polyvinylidene chloride, polyamide, polyethylene terephthalate, and polybutylene terephthalate, various resins such as polyether, polyvinyl alcohol, polyvinylpyrrolidone, and copolymers thereof, and various organic binders such as various waxes, paraffins, higher fatty acids (such as stearic acid), higher alcohols, higher fatty acid esters, and higher fatty acid amides. These can be used alone or by mixing two or more types thereof.
The content of the binder is preferably about 2 mass % or more and 20 mass % or less, more preferably about 5 mass % or more and 10 mass % or less with respect to the total amount of the kneaded material. By setting the content of the binder within the above range, a molded body can be formed with good moldability, and also the density is increased, and thus, the stability of the shape of the molded body and the like can be particularly enhanced. Further, according to this, a difference in size between the molded body and the degreased body, that is, a so-called shrinkage ratio is optimized, whereby a decrease in the dimensional accuracy of the finally obtained sintered body can be prevented. That is, a sintered body having a high density and high dimensional accuracy can be obtained.
In the kneaded material, a plasticizer may be added as needed. Examples of the plasticizer include phthalate esters (such as DOP, DEP, and DBP), adipate esters, trimellitate esters, and sebacate esters. These can be used alone or by mixing two or more types thereof.
Further, in the kneaded material, other than the metal powder for powder metallurgy, the binder, and the plasticizer, for example, any of a variety of additives such as a lubricant, an antioxidant, a degreasing accelerator, and a surfactant can be added as needed.
The kneading conditions vary depending on the respective conditions such as the metal composition or the particle diameter of the metal powder for powder metallurgy to be used, the composition of the binder, and the blending amount thereof. However, for example, the kneading temperature can be set to about 50° C. or higher and 200° C. or lower, and the kneading time can be set to about 15 minutes or more and 210 minutes or less.
Further, the kneaded material is formed into a pellet (small particle) as needed. The particle diameter of the pellet is set to, for example, about 1 mm or more and 15 mm or less.
Incidentally, depending on the molding method described below, in place of the kneaded material, a granulated powder may be produced. The kneaded material, the granulated powder, and the like are examples of the composition to be subjected to the molding step described below.
In the embodiment of the granulated powder according to the invention, the metal powder for powder metallurgy according to the invention is subjected to a granulation treatment, whereby a plurality of metal particles are bound to one another with the binder. According to this, a granulated powder capable of producing a sintered body having a high density is obtained.
Examples of the binder to be used for producing the granulated powder include polyolefins such as polyethylene, polypropylene, and ethylene-vinyl acetate copolymers, acrylic resins such as polymethyl methacrylate and polybutyl methacrylate, styrenic resins such as polystyrene, polyesters such as polyvinyl chloride, polyvinylidene chloride, polyamide, polyethylene terephthalate, and polybutylene terephthalate, various resins such as polyether, polyvinyl alcohol, polyvinylpyrrolidone, and copolymers thereof, and various organic binders such as various waxes, paraffins, higher fatty acids (such as stearic acid), higher alcohols, higher fatty acid esters, and higher fatty acid amides. These can be used alone or by mixing two or more types thereof.
Among these, as the binder, a binder containing a polyvinyl alcohol or polyvinylpyrrolidone is preferred. These binder components have a high binding ability, and therefore can efficiently form the granulated powder even if the amount thereof is relatively small. Further, the thermal decomposability thereof is also high, and therefore, the binder can be reliably decomposed and removed in a short time during degreasing and firing.
The content of the binder is preferably about 0.2 mass % or more and 10 mass % or less, more preferably about 0.3 mass % or more and 5 mass % or less, further more preferably about 0.3 mass % or more and 2 mass % or less with respect to the total amount of the granulated powder. By setting the content of the binder within the above range, the granulated powder can be efficiently formed while preventing significantly large particles from being formed or a large amount of the metal particles which are not granulated from remaining. Further, since the moldability is improved, the stability of the shape of the molded body and the like can be particularly enhanced. Further, by setting the content of the binder within the above range, a difference in size between the molded body and the degreased body, that is, a so-called shrinkage ratio is optimized, whereby a decrease in the dimensional accuracy of the finally obtained sintered body can be prevented.
Further, in the granulated powder, any of a variety of additives such as a plasticizer, a lubricant, an antioxidant, a degreasing accelerator, and a surfactant may be added as needed.
Examples of the granulation treatment include a spray drying method, a tumbling granulation method, a fluidized bed granulation method, and a tumbling fluidized bed granulation method.
In the granulation treatment, a solvent which dissolves the binder is used as needed. Examples of the solvent include inorganic solvents such as water and carbon tetrachloride, and organic solvents such as ketone-based solvents, alcohol-based solvents, ether-based solvents, cellosolve-based solvents, aliphatic hydrocarbon-based solvents, aromatic hydrocarbon-based solvents, aromatic heterocyclic compound-based solvents, amide-based solvents, halogen compound-based solvents, ester-based solvents, amine-based solvents, nitrile-based solvents, nitro-based solvents, and aldehyde-based solvents, and one type or a mixture of two or more types selected from these solvents is used.
The average particle diameter of the granulated powder is not particularly limited, but is preferably about 10 μm or more and 200 μm or less, more preferably about 20 μm or more and 100 μm or less, further more preferably about 25 μm or more and 60 μm or less. The granulated powder having such a particle diameter has favorable fluidity, and can more faithfully reflect the shape of a molding die.
The average particle diameter is obtained as a particle diameter when the cumulative amount from the small diameter side reaches 50% in a cumulative particle size distribution on a mass basis obtained by laser diffractometry.
(B) Molding Step
Subsequently, the kneaded material or the granulated powder is molded, whereby a molded body having the same shape as that of a target sintered body is produced.
The method for producing a molded body (molding method) is not particularly limited, and for example, any of a variety of molding methods such as a powder compaction molding (compression molding) method, a metal injection molding (MIM) method, and an extrusion molding method can be used.
The molding conditions in the case of a powder compaction molding method among these methods are preferably such that the molding pressure is about 200 MPa or more and 1000 MPa or less (2 t/cm2 or more and 10 t/cm2 or less), which vary depending on the respective conditions such as the composition and the particle diameter of the metal powder for powder metallurgy to be used, the composition of the binder, and the blending amount thereof.
The molding conditions in the case of a metal injection molding method are preferably such that the material temperature is about 80° C. or higher and 210° C. or lower, and the injection pressure is about 50 MPa or more and 500 MPa or less (0.5 t/cm2 or more and 5 t/cm2 or less), which vary depending on the respective conditions.
The molding conditions in the case of an extrusion molding method are preferably such that the material temperature is about 80° C. or higher and 210° C. or lower, and the extrusion pressure is about 50 MPa or more and 500 MPa or less (0.5 t/cm2 or more and 5 t/cm2 or less), which vary depending on the respective conditions.
The thus obtained molded body is in a state where the binder is uniformly distributed in gaps between the particles of the metal powder.
The shape and size of the molded body to be produced are determined in anticipation of shrinkage of the molded body in the subsequent degreasing step and firing step.
(C) Degreasing Step
Subsequently, the thus obtained molded body is subjected to a degreasing treatment (binder removal treatment), whereby a degreased body is obtained.
Specifically, the degreasing treatment is performed by heating the molded body to decompose the binder, thereby removing the binder from the molded body.
Examples of the degreasing treatment include a method of heating the molded body and a method of exposing the molded body to a gas capable of decomposing the binder.
In the case of using a method of heating the molded body, the conditions for heating the molded body are preferably such that the temperature is about 100° C. or higher and 750° C. or lower and the time is about 0.1 hours or more and 20 hours or less, and more preferably such that the temperature is about 150° C. or higher and 600° C. or lower and the time is about 0.5 hours or more and 15 hours or less, which slightly vary depending on the composition and the blending amount of the binder. According to this, the degreasing of the molded body can be performed necessarily and sufficiently without sintering the molded body. As a result, it is possible to reliably prevent a large amount of the binder component from remaining inside the degreased body.
The atmosphere when the molded body is heated is not particularly limited, and an atmosphere of a reducing gas such as hydrogen, an atmosphere of an inert gas such as nitrogen or argon, an atmosphere of an oxidative gas such as air, a reduced pressure atmosphere obtained by reducing the pressure of such an atmosphere, or the like can be used.
Examples of the gas capable of decomposing the binder include ozone gas.
Incidentally, by dividing this degreasing step into a plurality of steps in which the degreasing conditions are different, and performing the plurality of steps, the binder in the molded body can be more rapidly decomposed and removed so that the binder does not remain in the molded body.
Further, according to need, the degreased body may be subjected to a machining process such as grinding, polishing, or cutting. The degreased body has a relatively low hardness and relatively high plasticity, and therefore, the machining process can be easily performed while preventing the degreased body from losing its shape. According to such a machining process, a sintered body having high dimensional accuracy can be easily obtained in the end.
(D) Firing Step
The degreased body obtained in the above step (C) is fired in a firing furnace, whereby a sintered body is obtained.
By this firing, in the metal powder for powder metallurgy, diffusion occurs at the boundary surface between the particles, resulting in sintering. At this time, by the mechanism as described above, the degreased body is rapidly sintered. As a result, a sintered body which is dense and has a high density on the whole is obtained.
The firing temperature varies depending on the composition, the particle diameter, and the like of the metal powder for powder metallurgy used in the production of the molded body and the degreased body, but is set to, for example, about 980° C. or higher and 1330° C. or lower, and preferably set to about 1050° C. or higher and 1260° C. or lower.
Further, the firing time is set to 0.2 hours or more and 7 hours or less, but is preferably set to about 1 hour or more and 6 hours or less.
In the firing step, the firing temperature or the below-described firing atmosphere may be changed in the middle of the step.
By setting the firing conditions within such a range, it is possible to sufficiently sinter the entire degreased body while preventing the sintering from proceeding excessively to cause oversintering and increase the size of the crystal structure. As a result, a sintered body having a high density and particularly excellent mechanical properties can be obtained.
Further, since the firing temperature is a relatively low temperature, it is easy to control the heating temperature in the firing furnace to be constant, and therefore, also the temperature of the degreased body is likely to be constant. As a result, a more homogeneous sintered body can be produced.
Further, since the firing temperature as described above is a firing temperature which can be sufficiently realized using a common firing furnace, and therefore, an inexpensive firing furnace can be used, and also the running cost can be kept low. In other words, in the case where the temperature exceeds the above-mentioned firing temperature, it is necessary to employ an expensive firing furnace using a special heat resistant material, and also the running cost may be increased.
The atmosphere when performing firing is not particularly limited, however, in consideration of prevention of significant oxidation of the metal powder, an atmosphere of a reducing gas such as hydrogen, an atmosphere of an inert gas such as argon, a reduced pressure atmosphere obtained by reducing the pressure of such an atmosphere, or the like is preferably used.
The thus obtained sintered body is a sintered body in which Fe is contained as a principal component, Ni is contained in a proportion of 5 mass % or more and 20 mass % or less, Si is contained in a proportion of 0.3 mass % or more and 5.0 mass % or less, C is contained in a proportion of 0.005 mass % or more and 0.3 mass % or less, when one element selected from the group consisting of Ti, V, Y, Zr, Nb, Hf, and Ta is defined as a first element, and one element selected from the group, and having a higher group number in the periodic table than that of the first element or having the same group number in the periodic table as that of the first element and a higher period number in the periodic table than that of the first element is defined as a second element, the first element is contained in a proportion of 0.01 mass % or more and 0.7 mass % or less, and the second element is contained in a proportion of 0.01 mass % or more and 0.7 mass % or less.
Such a sintered body has a high density and excellent mechanical properties. That is, the sintered body has a higher relative density than a sintered body obtained by sintering a metal powder in the related art. Therefore, according to the invention, a sintered body having a high density which could not be obtained unless an additional treatment such as an HIP treatment is performed can be realized without performing an additional treatment.
Specifically, according to the invention, for example, the relative density can be expected to be increased by 2% or more as compared with the related art, which slightly varies depending on the composition of the metal powder for powder metallurgy.
As a result, the relative density of the obtained sintered body can be expected to be, for example, 97% or more (preferably 98% or more, more preferably 98.5% or more). The sintered body having a relative density within such a range has excellent mechanical properties comparable to those of ingot materials although it has a shape as close as possible to a desired shape by using a powder metallurgy technique, and therefore, the sintered body can be applied to a variety of machine components, structural components, and the like with virtually no post-processing.
Further, the tensile strength and the 0.2% proof stress of a sintered body produced by molding a composition containing the metal powder for powder metallurgy according to the invention and a binder, followed by degreasing and sintering are higher than those of a sintered body obtained by performing sintering in the same manner using a metal powder in the related art. This is considered to be because by optimizing the alloy composition, the sinterability of the metal powder is enhanced, and thus, the mechanical properties of a sintered body to be produced using the metal powder are enhanced.
The thus obtained sintered body has a sufficiently high density and excellent mechanical properties even without performing an additional treatment, however, in order to further increase the density and enhance the mechanical properties, a variety of additional treatments may be performed.
As the additional treatment, for example, an additional treatment of increasing the density such as the HIP treatment described above may be performed, and also a variety of quenching treatments, a variety of sub-zero treatments, a variety of tempering treatments, a variety of hardening treatments, and the like may be performed. These additional treatments may be performed alone or two or more treatments thereof may be performed in combination.
Among these, examples of the hardening treatment include a treatment in which after a solid solution heat treatment of performing quenching from a temperature of 1020° C. or higher and 1060° C. or lower is performed, a precipitation hardening heat treatment of performing air-cooling from a temperature of 470° C. or higher and 630° C. or lower is performed, and a treatment in which only the precipitation hardening heat treatment is performed. The duration of the temperature in the solid solution heat treatment is not particularly limited, but is preferably 1 minute or more and 40 minutes or less. Further, the duration of the time in the precipitation hardening heat treatment is not particularly limited, but is preferably 5 minutes or more and 5 hours or less. Further, such a hardening treatment may be performed as needed, and for example, in the case where a material is in a state of being subjected to a heat treatment equivalent to the above-mentioned hardening treatment as a result of the firing step, or the like, this treatment may be omitted.
According to the metal powder for powder metallurgy according to the invention, even if such a hardening treatment is performed at a relatively low temperature or even at a high temperature for a relatively short period of time, a sufficient effect for the improvement of the mechanical properties can be obtained. Because of this, while improving the mechanical properties accompanying the hardening treatment, the deformation of the sintered body accompanying the hardening treatment can be minimized, and the dimensional accuracy of the sintered body can be made closer to the desired value.
Further, in the above-mentioned firing step or a variety of additional treatments, alight element in the metal powder (in the sintered body) is volatilized, and the composition of the finally obtained sintered body slightly changes from the composition of the metal powder in some cases.
For example, the content of C in the final sintered body may change within the range of 5% or more and 100% or less (preferably within the range of 30% or more and 100% or less) of the content of C in the metal powder for powder metallurgy, which varies depending on the conditions for the step or the conditions for the treatment.
Further, also the content of O in the final sintered body may change within the range of 1% or more and 50% or less (preferably within the range of 3% or more and 50% or less) of the content of O in the metal powder for powder metallurgy, which varies depending on the conditions for the step or the conditions for the treatment.
On the other hand, as described above, the produced sintered body may be subjected to an HIP treatment as part of the additional treatments to be performed as needed. However, a sufficient effect is not exhibited even if an HIP treatment is performed in many cases. In the HIP treatment, the sintered body can be further densified, however, the sintered body obtained according to the invention has already been sufficiently densified at the end of the firing step. Therefore, even if the HIP treatment is further performed, further densification hardly proceeds.
In addition, in the HIP treatment, it is necessary to apply pressure to a material to be treated through a pressure medium, and therefore, the material to be treated may be contaminated, the composition or the physical properties of the material to be treated may unintentionally change due to the contamination, or the color of the material to be treated may change due to the contamination. Further, by the application of pressure, residual stress is generated or increased in the material to be treated, and a problem such as a change in the shape or a decrease in the dimensional accuracy may occur as the residual stress is released over time.
On the other hand, according to the invention, a sintered body having a sufficiently high density can be produced without performing such an HIP treatment, and therefore, a sintered body having an increased density and also an increased strength can be obtained in the same manner as in the case of performing an HIP treatment. Such a sintered body is less contaminated or discolored, and an unintended change in the composition or physical properties, or the like occurs less, and also a problem such as a change in the shape or a decrease in the dimensional accuracy occurs less. Therefore, according to the invention, a sintered body having high mechanical strength and dimensional accuracy, and excellent durability can be efficiently produced.
Further, a sintered body produced according to the invention tends to have a uniform composition and a uniform crystal structure in the entire sintered body. Due to this, the sintered body has high structural isotropy and therefore has excellent durability against a load from every direction regardless of its shape.
Incidentally, it is observed that in the thus obtained sintered body, the porosity near the surface is relatively smaller than the porosity inside the sintered body in many cases. The reason for this is not clear, however, one of the reasons is due to the fact that by adding the first element and the second element, a sintering reaction is more likely to proceed near the surface than inside the molded body.
Specifically, when the porosity near the surface of the sintered body is represented by A1 and the porosity inside the sintered body is represented by A2, A2−A1 is preferably 0.5% or more and 10% or less, more preferably 1% or more and 5% or less. The sintered body showing the value of A2−A1 within the above range not only has a necessary and sufficient mechanical strength, but also can easily flatten the surface. That is, by polishing the surface of such a sintered body, a surface having high specularity can be obtained.
Such a sintered body having high specularity not only has a high mechanical strength, but also has excellent aesthetic properties. Therefore, such a sintered body is favorably used also for application requiring excellent aesthetic appearance.
Incidentally, the porosity A1 near the surface of the sintered body refers to a porosity in a 25-μm radius region centered on the position at a depth of 50 μm from the surface of the cross section of the sintered body. Further, the porosity A2 inside the sintered body refers to a porosity in a 25-μm radius region centered on the position at a depth of 300 μm from the surface of the cross section of the sintered body. These porosities are values obtained by observing the cross section of the sintered body with a scanning electron microscope and dividing the area of pores present in the region by the area of the region.
Hereinabove, the metal powder for powder metallurgy, the compound, the granulated powder, and the sintered body according to the invention have been described with reference to preferred embodiments, however, the invention is not limited thereto.
Further, the sintered body according to the invention is used for, for example, parts for transport machinery such as parts for automobiles, parts for bicycles, parts for railroad cars, parts for ships, parts for airplanes, and parts for space transport machinery (such as rockets); parts for electronic devices such as parts for personal computers and parts for mobile phone terminals; parts for electrical devices such as refrigerators, washing machines, and cooling and heating machines; parts for machines such as machine tools and semiconductor production devices; parts for plants such as atomic power plants, thermal power plants, hydroelectric power plants, oil refinery plants, and chemical complexes; parts for timepieces, metallic tableware, jewels, ornaments such as frames for glasses, and all other sorts of structural parts.
In particular, the sintered body according to the invention can be also applied to various machine elements such as gears, pulleys, shafts, bearings, levers, wedges, wheels, screws, nuts, and links.
Next, Examples of the invention will be described.
1. Production of Sintered Body (Zr—Nb Based)
Sample No. 1
(1) First, a metal powder having a composition shown in Table 1 produced by a water atomization method was prepared.
The composition of the powder shown in Table 1 was identified and quantitatively determined by inductively coupled high-frequency plasma optical emission spectrometry (ICP analysis method). In the ICP analysis, an ICP device (model: CIROS-120) manufactured by Rigaku Corporation was used. Further, in the identification and quantitative determination of C, a carbon-sulfur analyzer (CS-200) manufactured by LECO Corporation was used. Further, in the identification and quantitative determination of O, an oxygen-nitrogen analyzer (TC-300/EF-300) manufactured by LECO Corporation was used.
(2) Subsequently, the metal powder and a mixture (organic binder) of polypropylene and a wax were weighed at a mass ratio of 9:1 and mixed with each other, whereby a mixed raw material was obtained.
(3) Subsequently, this mixed raw material was kneaded using a kneader, whereby a compound was obtained.
(4) Subsequently, this compound was molded using an injection molding machine under the following molding conditions, whereby a molded body was produced.
Molding Conditions
Material temperature: 150° C.
Injection pressure: 11 MPa (110 kgf/cm2)
(5) Subsequently, the obtained molded body was subjected to a heat treatment (degreasing treatment) under the following degreasing conditions, whereby a degreased body was obtained.
Degreasing Conditions
Degreasing temperature: 500° C.
Degreasing time: 1 hour (retention time at the degreasing temperature)
Degreasing atmosphere: nitrogen atmosphere
(6) Subsequently, the obtained degreased body was fired under the following firing conditions, whereby a sintered body was obtained. The shape of the sintered body was determined to be a cylindrical shape with a diameter of 10 mm and a thickness of 5 mm.
Firing Conditions
Firing temperature: 1200° C.
Firing time: 3 hours (retention time at the firing temperature)
Firing atmosphere: argon atmosphere
(7) Subsequently, the obtained sintered body was sequentially subjected to a solid solution heat treatment and a precipitation hardening heat treatment under the following conditions.
Conditions for Solid Solution Heat Treatment
Heating temperature: 1050° C.
Heating time: 10 minutes
Cooling method: water cooling
Conditions for Precipitation Hardening Heat Treatment
Heating temperature: 620° C.
Heating time: 60 minutes
Cooling method: air cooling
Sample Nos. 2 to 25
Sintered bodies were obtained in the same manner as the method for producing the sintered body of sample No. 1 except that the composition and the like of the metal powder for powder metallurgy were changed as shown in Table 1, respectively. Some sintered bodies were subjected to an HIP treatment under the following conditions after firing. Further, some other sintered bodies were obtained using a metal powder produced by a gas atomization method, respectively, and “Gas” is entered in the column of Remarks in Table 1.
HIP Treatment Conditions
Heating temperature: 1100° C.
Heating time: 2 hours
Applied pressure: 100 MPa
In Table 1, among the sintered bodies of the respective sample Nos., those corresponding to the invention are denoted by “Ex.” (Example), and those not corresponding to the invention are denoted by “Comp. Ex.” (Comparative Example).
Each sintered body contained very small amounts of impurities, but the description thereof in Table 1 is omitted.
Sample No. 26
(1) First, a metal powder having a composition shown in Table 2 was produced by a water atomization method in the same manner as in the case of sample No. 1.
(2) Subsequently, the metal powder was granulated by a spray drying method. The binder used at this time was polyvinyl alcohol, which was used in an amount of 1 part by mass with respect to 100 parts by mass of the metal powder. Further, a solvent (ion exchanged water) was used in an amount of 50 parts by mass with respect to 1 part by mass of polyvinyl alcohol. In this manner, a granulated powder having an average particle diameter of 50 μm was obtained.
(3) Subsequently, this granulated powder was subjected to powder compaction molding under the following molding conditions. In this molding, a press molding machine was used. The shape of the molded body to be produced was determined to be a cubic shape with a side length of 20 mm.
Molding Conditions
Material temperature: 90° C.
Molding pressure: 600 MPa (6 t/cm2)
(4) Subsequently, the obtained molded body was subjected to a heat treatment (degreasing treatment) under the following degreasing conditions, whereby a degreased body was obtained.
Degreasing Conditions
Degreasing temperature: 450° C.
Degreasing time: 2 hours (retention time at the degreasing temperature)
Degreasing atmosphere: nitrogen atmosphere
(5) Subsequently, the obtained degreased body was fired under the following firing conditions, whereby a sintered body was obtained.
Firing Conditions
Firing temperature: 1200° C.
Firing time: 3 hours (retention time at the firing temperature)
Firing atmosphere: argon atmosphere
(6) Subsequently, the obtained sintered body was sequentially subjected to a solid solution heat treatment and a precipitation hardening heat treatment under the following conditions.
Conditions for Solid Solution Heat Treatment
Heating temperature: 1050° C.
Heating time: 10 minutes
Cooling method: water cooling
Conditions for Precipitation Hardening Heat Treatment
Heating temperature: 480° C.
Heating time: 60 minutes
Cooling method: air cooling
Sample Nos. 27 to 41
Sintered bodies were obtained in the same manner as in the case of sample No. 26 except that the composition and the like of the metal powder for powder metallurgy were changed as shown in Table 2, respectively. Some sintered bodies were subjected to an HIP treatment under the following conditions after firing.
HIP Treatment Conditions
Heating temperature: 1100° C.
Heating time: 2 hours
Applied pressure: 100 MPa
In Table 2, among the sintered bodies of the respective sample Nos., those corresponding to the invention are denoted by “Ex.” (Example), and those not corresponding to the invention are denoted by “Comp. Ex.” (Comparative Example).
Each sintered body contained very small amounts of impurities, but the description thereof in Table 2 is omitted.
2. Evaluation of Sintered Body (Zr—Nb Based)
2.1 Evaluation of Relative Density
With respect to the sintered bodies of the respective sample Nos. shown in Tables 1 and 2, the sintered density was measured in accordance with the method for measuring the density of sintered metal materials specified in JIS Z 2501 (2000), and also the relative density of each sintered body was calculated with reference to the true density of the metal powder for powder metallurgy used for producing each sintered body.
The calculation results are shown in Tables 3 and 4.
2.2 Evaluation of Hardness
With respect to the sintered bodies of the respective sample Nos. shown in Tables 1 and 2, the Vickers hardness was measured in accordance with the Vickers hardness test method specified in JIS Z 2244 (2009).
Then, the measured hardness was evaluated according to the following evaluation criteria.
Evaluation Criteria for Vickers Hardness
A: The Vickers hardness is particularly high.
B: The Vickers hardness is high.
C: The Vickers hardness is somewhat high.
D: The Vickers hardness is somewhat low.
E: The Vickers hardness is low.
F: The Vickers hardness is particularly low.
The evaluation results are shown in Tables 3 and 4.
2.3 Evaluation of Tensile Strength, 0.2% Proof Stress, and Elongation
With respect to the sintered bodies of the respective sample Nos. shown in Tables 1 and 2, the tensile strength, 0.2% proof stress, and elongation were measured in accordance with the metal material tensile test method specified in JIS Z 2241 (2011).
Then, the measured physical property values were evaluated according to the following evaluation criteria.
Evaluation Criteria for Tensile Strength
A: The tensile strength of the sintered body is particularly high.
B: The tensile strength of the sintered body is high.
C: The tensile strength of the sintered body is somewhat high.
D: The tensile strength of the sintered body is somewhat low.
E: The tensile strength of the sintered body is low.
F: The tensile strength of the sintered body is particularly low.
Evaluation Criteria for 0.2% Proof Stress
A: The 0.2% proof stress of the sintered body is particularly high.
B: The 0.2% proof stress of the sintered body is high.
C: The 0.2% proof stress of the sintered body is somewhat high.
D: The 0.2% proof stress of the sintered body is somewhat low.
E: The 0.2% proof stress of the sintered body is low.
F: The 0.2% proof stress of the sintered body is particularly low.
Evaluation Criteria for Elongation
A: The elongation of the sintered body is particularly high.
B: The elongation of the sintered body is high.
C: The elongation of the sintered body is somewhat high.
D: The elongation of the sintered body is somewhat low.
E: The elongation of the sintered body is low.
F: The elongation of the sintered body is particularly low.
The above evaluation results are shown in Tables 3 and 4.
2.4 Evaluation of Fatigue Strength
With respect to the sintered bodies of the respective sample Nos. shown in Tables 1 and 2, the fatigue strength was measured.
The fatigue strength was measured in accordance with the test method specified in JIS Z 2273 (1978). The waveform of an applied load corresponding to a repeated stress was set to an alternating sine wave, and the minimum/maximum stress ratio (minimum stress/maximum stress) was set to 0.1. Further, the repeated frequency was set to 30 Hz, and the repeat count was set to 1×107.
Then, the measured fatigue strength was evaluated according to the following evaluation criteria.
Evaluation Criteria for Fatigue Strength
A: The fatigue strength of the sintered body is particularly high.
B: The fatigue strength of the sintered body is high.
C: The fatigue strength of the sintered body is somewhat high.
D: The fatigue strength of the sintered body is somewhat low.
E: The fatigue strength of the sintered body is low.
F: The fatigue strength of the sintered body is particularly low.
The above evaluation results are shown in Tables 3 and 4.
2.5 Evaluation of Corrosion Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Tables 1 and 2, the corrosion resistance was measured.
Specifically, first, a test piece cut out from each of the sintered bodies of the respective sample Nos. was prepared.
Subsequently, a salt spray test was performed for the test piece in accordance with the Method of salt spray testing specified in JIS Z 2371: 2000. The testing time was set to 24 hours and 48 hours.
Then, the test piece after the test was evaluated according to the following evaluation criteria.
Evaluation Criteria for Salt Spray Test
A: No corrosion is observed.
B: Very little corrosion is observed.
C: Somewhat little corrosion is observed.
D: Somewhat much corrosion is observed.
E: Much corrosion is observed.
F: Particularly much corrosion is observed.
The above evaluation results are shown in Tables 3 and 4.
2.6. Evaluation of Wear Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Tables 1 and 2, the wear resistance was measured.
Specifically, first, a disk-shaped test piece cut out from each of the sintered bodies of the respective sample Nos. was prepared.
Subsequently, the surface of the test piece was subjected to a buff polishing treatment. Subsequently, for the polished surface, a wear resistance test was performed in accordance with Testing method for wear resistance of fine ceramics by ball-on-disc method specified in JIS R 1613 (2010), and a wear amount of the disk-shaped (annular) test piece was measured. The measurement conditions are as follows.
Measurement Conditions for Specific Wear Amount
Material of spherical test piece: high carbon chromium bearing steel (SUJ2)
Size of spherical test piece: 6 mm in diameter
Material of disk-shaped (annular) test piece: each of sintered bodies of respective Sample Nos.
Size of disk-shaped (annular) test piece: 10 mm in diameter
Magnitude of load: 10 N
Sliding rate: 0.1 m/s
Sliding circle diameter: 30 mm
Sliding distance: 50 m
The thus measured wear amount was evaluated according to the following evaluation criteria.
Evaluation Criteria for Wear Amount
A: The wear amount is particularly small.
B: The wear amount is small.
C: The wear amount is somewhat small.
D: The wear amount is somewhat large.
E: The wear amount is large.
F: The wear amount is particularly large.
The above evaluation results are shown in Tables 3 and 4.
2.7 Evaluation of Dimensional Accuracy
With respect to the sintered bodies of the respective sample Nos. shown in Tables 1 and 2, the dimensional accuracy was measured.
Specifically, first, the dimensions of the respective Sample Nos. were measured.
Subsequently, a dimensional difference between the target value and the measurement value of the dimension of the sintered body was calculated and the obtained dimensional difference was evaluated according to the following evaluation criteria.
Evaluation Criteria for Dimensional Accuracy
A: The dimensional accuracy is particularly high (the dimensional difference is particularly small).
B: The dimensional accuracy is high (the dimensional difference is small).
C: The dimensional accuracy is somewhat high (the dimensional difference is somewhat small).
D: The dimensional accuracy is somewhat low (the dimensional difference is somewhat large).
E: The dimensional accuracy is low (the dimensional difference is large).
F: The dimensional accuracy is particularly low (the dimensional difference is particularly large).
The above evaluation results are shown in Tables 3 and 4.
As apparent from Tables 3 and 4, it was confirmed that the sintered bodies corresponding to Example each have a higher relative density than the sintered bodies corresponding to Comparative Example (excluding the sintered bodies having undergone the HIP treatment). It was also confirmed that there is a significant difference in properties such as tensile strength, 0.2% proof stress, and elongation between them. Further, it was also confirmed that there is a significant difference in corrosion resistance, wear resistance, and dimensional accuracy between them.
On the other hand, when the respective physical property values were compared between the sintered bodies corresponding to Example and the sintered bodies having undergone the HIP treatment, it was confirmed that the physical property values are all comparable to each other.
3. Production of Sintered Body (Hf—Nb Based)
Sample Nos. 42 to 66
Sintered bodies were obtained in the same manner as the method for producing the sintered body of sample No. 1 except that the composition and the like of the metal powder for powder metallurgy were changed as shown in Table 5, respectively. Further, some sintered bodies were subjected to an HIP treatment under the following conditions after firing.
HIP Treatment Conditions
Heating temperature: 1100° C.
Heating time: 2 hours
Applied pressure: 100 MPa
In Table 5, among the sintered bodies of the respective sample Nos., those corresponding to the invention are denoted by “Ex.” (Example), and those not corresponding to the invention are denoted by “Comp. Ex.” (Comparative Example).
Each sintered body contained very small amounts of impurities, but the description thereof in Table 5 is omitted.
4. Evaluation of Sintered Body (Hf—Nb Based)
4.1 Evaluation of Relative Density
With respect to the sintered bodies of the respective sample Nos. shown in Table 5, the sintered density was measured in accordance with the method for measuring the density of sintered metal materials specified in JIS Z 2501 (2000), and also the relative density of each sintered body was calculated with reference to the true density of the metal powder for powder metallurgy used for producing each sintered body.
The calculation results are shown in Table 6.
4.2 Evaluation of Hardness
With respect to the sintered bodies of the respective sample Nos. shown in Table 5, the Vickers hardness was measured in accordance with the Vickers hardness test method specified in JIS Z 2244 (2009).
Then, the measured hardness was evaluated according to the evaluation criteria described in 2.2.
The evaluation results are shown in Table 6.
4.3 Evaluation of Tensile Strength, 0.2% Proof Stress, and Elongation
With respect to the sintered bodies of the respective sample Nos. shown in Table 5, the tensile strength, 0.2% proof stress, and elongation were measured in accordance with the metal material tensile test method specified in JIS Z 2241 (2011).
Then, the measured physical property values were evaluated according to the evaluation criteria described in 2.3.
The evaluation results are shown in Table 6.
4.4 Evaluation of Fatigue Strength
With respect to the sintered bodies of the respective sample Nos. shown in Table 5, the fatigue strength was measured in the same manner as in 2.4.
Then, the measured fatigue strength was evaluated according to the evaluation criteria described in 2.4.
The evaluation results are shown in Table 6.
4.5 Evaluation of Corrosion Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 5, the corrosion resistance was measured in the same manner as in 2.5.
Then, the measured corrosion resistance was evaluated according to the evaluation criteria described in 2.5.
The evaluation results are shown in Table 6.
4.6 Evaluation of Wear Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 5, the wear resistance was measured in the same manner as in 2.6.
Then, the measured wear resistance was evaluated according to the evaluation criteria described in 2.6.
The evaluation results are shown in Table 6.
4.7 Evaluation of Dimensional Accuracy
With respect to the sintered bodies of the respective sample Nos. shown in Table 5, the dimensional accuracy was measured in the same manner as in 2.7.
Then, the measured dimensional accuracy was evaluated according to the evaluation criteria described in 2.7.
The evaluation results are shown in Table 6.
As apparent from Table 6, it was confirmed that the sintered bodies corresponding to Example each have a higher relative density than the sintered bodies corresponding to Comparative Example (excluding the sintered bodies having undergone the HIP treatment). It was also confirmed that there is a significant difference in properties such as tensile strength, 0.2% proof stress, and elongation between them. Further, it was also confirmed that there is a significant difference in corrosion resistance, wear resistance, and dimensional accuracy between them.
On the other hand, when the respective physical property values were compared between the sintered bodies corresponding to Example and the sintered bodies having undergone the HIP treatment, it was confirmed that the physical property values are all comparable to each other.
5. Production of Sintered Body (Ti—Nb Based)
Sample Nos. 67 to 81
Sintered bodies were obtained in the same manner as the method for producing the sintered body of sample No. 1 except that the composition and the like of the metal powder for powder metallurgy were changed as shown in Table 7, respectively.
In Table 7, among the sintered bodies of the respective sample Nos., those corresponding to the invention are denoted by “Ex.” (Example), and those not corresponding to the invention are denoted by “Comp. Ex.” (Comparative Example).
Each sintered body contained very small amounts of impurities, but the description thereof in Table 7 is omitted.
6. Evaluation of Sintered Body (Ti—Nb Based)
6.1 Evaluation of Relative Density
With respect to the sintered bodies of the respective sample Nos. shown in Table 7, the sintered density was measured in accordance with the method for measuring the density of sintered metal materials specified in JIS Z 2501 (2000), and also the relative density of each sintered body was calculated with reference to the true density of the metal powder for powder metallurgy used for producing each sintered body.
The calculation results are shown in Table 8.
6.2 Evaluation of Hardness
With respect to the sintered bodies of the respective sample Nos. shown in Table 7, the Vickers hardness was measured in accordance with the Vickers hardness test method specified in JIS Z 2244 (2009).
Then, the measured hardness was evaluated according to the evaluation criteria described in 2.2.
The evaluation results are shown in Table 8.
6.3 Evaluation of Tensile Strength, 0.2% Proof Stress, and Elongation
With respect to the sintered bodies of the respective sample Nos. shown in Table 7, the tensile strength, 0.2% proof stress, and elongation were measured in accordance with the metal material tensile test method specified in JIS Z 2241 (2011).
Then, the measured physical property values were evaluated according to the evaluation criteria described in 2.3.
The evaluation results are shown in Table 8.
6.4 Evaluation of Fatigue Strength
With respect to the sintered bodies of the respective sample Nos. shown in Table 7, the fatigue strength was measured in the same manner as in 2.4.
Then, the measured fatigue strength was evaluated according to the evaluation criteria described in 2.4.
The evaluation results are shown in Table 8.
6.5 Evaluation of Corrosion Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 7, the corrosion resistance was measured in the same manner as in 2.5.
Then, the measured corrosion resistance was evaluated according to the evaluation criteria described in 2.5.
The evaluation results are shown in Table 8.
6.6 Evaluation of Wear Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 7, the wear resistance was measured in the same manner as in 2.6.
Then, the measured wear resistance was evaluated according to the evaluation criteria described in 2.6.
The evaluation results are shown in Table 8.
6.7 Evaluation of Dimensional Accuracy
With respect to the sintered bodies of the respective sample Nos. shown in Table 7, the dimensional accuracy was measured in the same manner as in 2.7.
Then, the measured dimensional accuracy was evaluated according to the evaluation criteria described in 2.7.
The evaluation results are shown in Table 8.
As apparent from Table 8, it was confirmed that the sintered bodies corresponding to Example each have a higher relative density than the sintered bodies corresponding to Comparative Example. It was also confirmed that there is a significant difference in properties such as tensile strength, 0.2% proof stress, and elongation between them. Further, it was also confirmed that there is a significant difference in corrosion resistance, wear resistance, and dimensional accuracy between them.
7. Production of Sintered Body (Nb—Ta Based)
Sample Nos. 82 to 92
Sintered bodies were obtained in the same manner as the method for producing the sintered body of sample No. 1 except that the composition and the like of the metal powder for powder metallurgy were changed as shown in Table 9, respectively.
In Table 9, among the sintered bodies of the respective sample Nos., those corresponding to the invention are denoted by “Ex.” (Example), and those not corresponding to the invention are denoted by “Comp. Ex.” (Comparative Example).
Each sintered body contained very small amounts of impurities, but the description thereof in Table 9 is omitted.
8. Evaluation of Sintered Body (Nb—Ta Based)
8.1 Evaluation of Relative Density
With respect to the sintered bodies of the respective sample Nos. shown in Table 9, the sintered density was measured in accordance with the method for measuring the density of sintered metal materials specified in JIS Z 2501 (2000), and also the relative density of each sintered body was calculated with reference to the true density of the metal powder for powder metallurgy used for producing each sintered body.
The calculation results are shown in Table 10.
8.2 Evaluation of Hardness
With respect to the sintered bodies of the respective sample Nos. shown in Table 9, the Vickers hardness was measured in accordance with the Vickers hardness test method specified in JIS Z 2244 (2009).
Then, the measured hardness was evaluated according to the evaluation criteria described in 2.2.
The evaluation results are shown in Table 10.
8.3 Evaluation of Tensile Strength, 0.2% Proof Stress, and Elongation
With respect to the sintered bodies of the respective sample Nos. shown in Table 9, the tensile strength, 0.2% proof stress, and elongation were measured in accordance with the metal material tensile test method specified in JIS Z 2241 (2011).
Then, the measured physical property values were evaluated according to the evaluation criteria described in 2.3.
The evaluation results are shown in Table 10.
8.4 Evaluation of Fatigue Strength
With respect to the sintered bodies of the respective sample Nos. shown in Table 9, the fatigue strength was measured in the same manner as in 2.4.
Then, the measured fatigue strength was evaluated according to the evaluation criteria described in 2.4.
The evaluation results are shown in Table 10.
8.5 Evaluation of Corrosion Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 9, the corrosion resistance was measured in the same manner as in 2.5.
Then, the measured corrosion resistance was evaluated according to the evaluation criteria described in 2.5.
The evaluation results are shown in Table 10.
8.6 Evaluation of Wear Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 9, the wear resistance was measured in the same manner as in 2.6.
Then, the measured wear resistance was evaluated according to the evaluation criteria described in 2.6.
The evaluation results are shown in Table 10.
8.7 Evaluation of Dimensional Accuracy
With respect to the sintered bodies of the respective sample Nos. shown in Table 9, the dimensional accuracy was measured in the same manner as in 2.7.
Then, the measured dimensional accuracy was evaluated according to the evaluation criteria described in 2.7.
The evaluation results are shown in Table 10.
As apparent from Table 10, it was confirmed that the sintered bodies corresponding to Example each have a higher relative density than the sintered bodies corresponding to Comparative Example. It was also confirmed that there is a significant difference in properties such as tensile strength, 0.2% proof stress, and elongation between them. Further, it was also confirmed that there is a significant difference in corrosion resistance, wear resistance, and dimensional accuracy between them.
9. Production of Sintered Body (Y—Nb Based)
Sample Nos. 93 to 105
Sintered bodies were obtained in the same manner as the method for producing the sintered body of sample No. 1 except that the composition and the like of the metal powder for powder metallurgy were changed as shown in Table 11, respectively.
In Table 11, among the sintered bodies of the respective sample Nos., those corresponding to the invention are denoted by “Ex.” (Example), and those not corresponding to the invention are denoted by “Comp. Ex.” (Comparative Example).
Each sintered body contained very small amounts of impurities, but the description thereof in Table 11 is omitted.
10. Evaluation of Sintered Body (Y—Nb Based)
10.1 Evaluation of Relative Density
With respect to the sintered bodies of the respective sample Nos. shown in Table 11, the sintered density was measured in accordance with the method for measuring the density of sintered metal materials specified in JIS Z 2501 (2000), and also the relative density of each sintered body was calculated with reference to the true density of the metal powder for powder metallurgy used for producing each sintered body.
The calculation results are shown in Table 12.
10.2 Evaluation of Hardness
With respect to the sintered bodies of the respective sample Nos. shown in Table 11, the Vickers hardness was measured in accordance with the Vickers hardness test method specified in JIS Z 2244 (2009).
Then, the measured hardness was evaluated according to the evaluation criteria described in 2.2.
The evaluation results are shown in Table 12.
10.3 Evaluation of Tensile Strength, 0.2% Proof Stress, and Elongation
With respect to the sintered bodies of the respective sample Nos. shown in Table 11, the tensile strength, 0.2% proof stress, and elongation were measured in accordance with the metal material tensile test method specified in JIS Z 2241 (2011).
Then, the measured physical property values were evaluated according to the evaluation criteria described in 2.3.
The evaluation results are shown in Table 12.
10.4 Evaluation of Fatigue Strength
With respect to the sintered bodies of the respective sample Nos. shown in Table 11, the fatigue strength was measured in the same manner as in 2.4.
Then, the measured fatigue strength was evaluated according to the evaluation criteria described in 2.4.
The evaluation results are shown in Table 12.
10.5 Evaluation of Corrosion Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 11, the corrosion resistance was measured in the same manner as in 2.5.
Then, the measured corrosion resistance was evaluated according to the evaluation criteria described in 2.5.
The evaluation results are shown in Table 12.
10.6 Evaluation of Wear Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 11, the wear resistance was measured in the same manner as in 2.6.
Then, the measured wear resistance was evaluated according to the evaluation criteria described in 2.6.
The evaluation results are shown in Table 12.
10.7 Evaluation of Dimensional Accuracy
With respect to the sintered bodies of the respective sample Nos. shown in Table 11, the dimensional accuracy was measured in the same manner as in 2.7.
Then, the measured dimensional accuracy was evaluated according to the evaluation criteria described in 2.7.
The evaluation results are shown in Table 12.
As apparent from Table 12, it was confirmed that the sintered bodies corresponding to Example each have a higher relative density than the sintered bodies corresponding to Comparative Example. It was also confirmed that there is a significant difference in properties such as tensile strength, 0.2% proof stress, and elongation between them. Further, it was also confirmed that there is a significant difference in corrosion resistance, wear resistance, and dimensional accuracy between them.
11. Production of Sintered Body (V—Nb Based)
Sample Nos. 106 to 118
Sintered bodies were obtained in the same manner as the method for producing the sintered body of sample No. 1 except that the composition and the like of the metal powder for powder metallurgy were changed as shown in Table 13, respectively.
In Table 13, among the sintered bodies of the respective sample Nos., those corresponding to the invention are denoted by “Ex.” (Example), and those not corresponding to the invention are denoted by “Comp. Ex.” (Comparative Example).
Each sintered body contained very small amounts of impurities, but the description thereof in Table 13 is omitted.
12. Evaluation of Sintered Body (V—Nb Based)
12.1 Evaluation of Relative Density
With respect to the sintered bodies of the respective sample Nos. shown in Table 13, the sintered density was measured in accordance with the method for measuring the density of sintered metal materials specified in JIS Z 2501 (2000), and also the relative density of each sintered body was calculated with reference to the true density of the metal powder for powder metallurgy used for producing each sintered body.
The calculation results are shown in Table 14.
12.2 Evaluation of Hardness
With respect to the sintered bodies of the respective sample Nos. shown in Table 13, the Vickers hardness was measured in accordance with the Vickers hardness test method specified in JIS Z 2244 (2009).
Then, the measured hardness was evaluated according to the evaluation criteria described in 2.2.
The evaluation results are shown in Table 14.
12.3 Evaluation of Tensile Strength, 0.2% Proof Stress, and Elongation
With respect to the sintered bodies of the respective sample Nos. shown in Table 13, the tensile strength, 0.2% proof stress, and elongation were measured in accordance with the metal material tensile test method specified in JIS Z 2241 (2011).
Then, the measured physical property values were evaluated according to the evaluation criteria described in 2.3.
The evaluation results are shown in Table 14.
12.4 Evaluation of Fatigue Strength
With respect to the sintered bodies of the respective sample Nos. shown in Table 13, the fatigue strength was measured in the same manner as in 2.4.
Then, the measured fatigue strength was evaluated according to the evaluation criteria described in 2.4.
The evaluation results are shown in Table 14.
12.5 Evaluation of Corrosion Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 13, the corrosion resistance was measured in the same manner as in 2.5.
Then, the measured corrosion resistance was evaluated according to the evaluation criteria described in 2.5.
The evaluation results are shown in Table 14.
12.6 Evaluation of Wear Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 13, the wear resistance was measured in the same manner as in 2.6.
Then, the measured wear resistance was evaluated according to the evaluation criteria described in 2.6.
The evaluation results are shown in Table 14.
12.7 Evaluation of Dimensional Accuracy
With respect to the sintered bodies of the respective sample Nos. shown in Table 13, the dimensional accuracy was measured in the same manner as in 2.7.
Then, the measured dimensional accuracy was evaluated according to the evaluation criteria described in 2.7.
The evaluation results are shown in Table 14.
As apparent from Table 14, it was confirmed that the sintered bodies corresponding to Example each have a higher relative density than the sintered bodies corresponding to Comparative Example. It was also confirmed that there is a significant difference in properties such as tensile strength, 0.2% proof stress, and elongation between them. Further, it was also confirmed that there is a significant difference in corrosion resistance, wear resistance, and dimensional accuracy between them.
13. Production of Sintered Body (Ti—Zr Based)
Sample Nos. 119 to 131
Sintered bodies were obtained in the same manner as the method for producing the sintered body of sample No. 1 except that the composition and the like of the metal powder for powder metallurgy were changed as shown in Table 15, respectively.
In Table 15, among the sintered bodies of the respective sample Nos., those corresponding to the invention are denoted by “Ex.” (Example), and those not corresponding to the invention are denoted by “Comp. Ex.” (Comparative Example).
Each sintered body contained very small amounts of impurities, but the description thereof in Table 15 is omitted.
14. Evaluation of Sintered Body (Ti—Zr Based)
14.1 Evaluation of Relative Density
With respect to the sintered bodies of the respective sample Nos. shown in Table 15, the sintered density was measured in accordance with the method for measuring the density of sintered metal materials specified in JIS Z 2501 (2000), and also the relative density of each sintered body was calculated with reference to the true density of the metal powder for powder metallurgy used for producing each sintered body.
The calculation results are shown in Table 16.
14.2 Evaluation of Hardness
With respect to the sintered bodies of the respective sample Nos. shown in Table 15, the Vickers hardness was measured in accordance with the Vickers hardness test method specified in JIS Z 2244 (2009).
Then, the measured hardness was evaluated according to the evaluation criteria described in 2.2.
The evaluation results are shown in Table 16.
14.3 Evaluation of Tensile Strength, 0.2% Proof Stress, and Elongation
With respect to the sintered bodies of the respective sample Nos. shown in Table 15, the tensile strength, 0.2% proof stress, and elongation were measured in accordance with the metal material tensile test method specified in JIS Z 2241 (2011).
Then, the measured physical property values were evaluated according to the evaluation criteria described in 2.3.
The evaluation results are shown in Table 16.
14.4 Evaluation of Fatigue Strength
With respect to the sintered bodies of the respective sample Nos. shown in Table 15, the fatigue strength was measured in the same manner as in 2.4.
Then, the measured fatigue strength was evaluated according to the evaluation criteria described in 2.4.
The evaluation results are shown in Table 16.
14.5 Evaluation of Corrosion Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 15, the corrosion resistance was measured in the same manner as in 2.5.
Then, the measured corrosion resistance was evaluated according to the evaluation criteria described in 2.5.
The evaluation results are shown in Table 16.
14.6 Evaluation of Wear Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 15, the wear resistance was measured in the same manner as in 2.6.
Then, the measured wear resistance was evaluated according to the evaluation criteria described in 2.6.
The evaluation results are shown in Table 16.
14.7 Evaluation of Dimensional Accuracy
With respect to the sintered bodies of the respective sample Nos. shown in Table 15, the dimensional accuracy was measured in the same manner as in 2.7.
Then, the measured dimensional accuracy was evaluated according to the evaluation criteria described in 2.7.
The evaluation results are shown in Table 16.
As apparent from Table 16, it was confirmed that the sintered bodies corresponding to Example each have a higher relative density than the sintered bodies corresponding to Comparative Example. It was also confirmed that there is a significant difference in properties such as tensile strength, 0.2% proof stress, and elongation between them. Further, it was also confirmed that there is a significant difference in corrosion resistance, wear resistance, and dimensional accuracy between them.
15. Production of Sintered Body (Zr—Ta Based)
Sample Nos. 132 to 142
Sintered bodies were obtained in the same manner as the method for producing the sintered body of sample No. 1 except that the composition and the like of the metal powder for powder metallurgy were changed as shown in Table 17, respectively.
In Table 17, among the sintered bodies of the respective sample Nos., those corresponding to the invention are denoted by “Ex.” (Example), and those not corresponding to the invention are denoted by “Comp. Ex.” (Comparative Example).
Each sintered body contained very small amounts of impurities, but the description thereof in Table 17 is omitted.
16. Evaluation of Sintered Body (Zr—Ta Based)
16.1 Evaluation of Relative Density
With respect to the sintered bodies of the respective sample Nos. shown in Table 17, the sintered density was measured in accordance with the method for measuring the density of sintered metal materials specified in JIS Z 2501 (2000), and also the relative density of each sintered body was calculated with reference to the true density of the metal powder for powder metallurgy used for producing each sintered body.
The calculation results are shown in Table 18.
16.2 Evaluation of Hardness
With respect to the sintered bodies of the respective sample Nos. shown in Table 17, the Vickers hardness was measured in accordance with the Vickers hardness test method specified in JIS Z 2244 (2009).
Then, the measured hardness was evaluated according to the evaluation criteria described in 2.2.
The evaluation results are shown in Table 18.
16.3 Evaluation of Tensile Strength, 0.2% Proof Stress, and Elongation
With respect to the sintered bodies of the respective sample Nos. shown in Table 17, the tensile strength, 0.2% proof stress, and elongation were measured in accordance with the metal material tensile test method specified in JIS Z 2241 (2011).
Then, the measured physical property values were evaluated according to the evaluation criteria described in 2.3.
The evaluation results are shown in Table 18.
16.4 Evaluation of Fatigue Strength
With respect to the sintered bodies of the respective sample Nos. shown in Table 17, the fatigue strength was measured in the same manner as in 2.4.
Then, the measured fatigue strength was evaluated according to the evaluation criteria described in 2.4.
The evaluation results are shown in Table 18.
16.5 Evaluation of Corrosion Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 17, the corrosion resistance was measured in the same manner as in 2.5.
Then, the measured corrosion resistance was evaluated according to the evaluation criteria described in 2.5.
The evaluation results are shown in Table 18.
16.6 Evaluation of Wear Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 17, the wear resistance was measured in the same manner as in 2.6.
Then, the measured wear resistance was evaluated according to the evaluation criteria described in 2.6.
The evaluation results are shown in Table 18.
16.7 Evaluation of Dimensional Accuracy
With respect to the sintered bodies of the respective sample Nos. shown in Table 17, the dimensional accuracy was measured in the same manner as in 2.7.
Then, the measured dimensional accuracy was evaluated according to the evaluation criteria described in 2.7.
The evaluation results are shown in Table 18.
As apparent from Table 18, it was confirmed that the sintered bodies corresponding to Example each have a higher relative density than the sintered bodies corresponding to Comparative Example. It was also confirmed that there is a significant difference in properties such as tensile strength, 0.2% proof stress, and elongation between them. Further, it was also confirmed that there is a significant difference in corrosion resistance, wear resistance, and dimensional accuracy between them.
17. Production of Sintered Body (Zr—V Based)
Sample Nos. 143 to 153
Sintered bodies were obtained in the same manner as the method for producing the sintered body of sample No. 1 except that the composition and the like of the metal powder for powder metallurgy were changed as shown in Table 19, respectively.
In Table 19, among the sintered bodies of the respective sample Nos., those corresponding to the invention are denoted by “Ex.” (Example), and those not corresponding to the invention are denoted by “Comp. Ex.” (Comparative Example).
Each sintered body contained very small amounts of impurities, but the description thereof in Table 19 is omitted.
18. Evaluation of Sintered Body (Zr—V Based)
18.1 Evaluation of Relative Density
With respect to the sintered bodies of the respective sample Nos. shown in Table 19, the sintered density was measured in accordance with the method for measuring the density of sintered metal materials specified in JIS Z 2501 (2000), and also the relative density of each sintered body was calculated with reference to the true density of the metal powder for powder metallurgy used for producing each sintered body.
The calculation results are shown in Table 20.
18.2 Evaluation of Hardness
With respect to the sintered bodies of the respective sample Nos. shown in Table 19, the Vickers hardness was measured in accordance with the Vickers hardness test method specified in JIS Z 2244 (2009).
Then, the measured hardness was evaluated according to the evaluation criteria described in 2.2.
The evaluation results are shown in Table 20.
18.3 Evaluation of Tensile Strength, 0.2% Proof Stress, and Elongation
With respect to the sintered bodies of the respective sample Nos. shown in Table 19, the tensile strength, 0.2% proof stress, and elongation were measured in accordance with the metal material tensile test method specified in JIS Z 2241 (2011).
Then, the measured physical property values were evaluated according to the evaluation criteria described in 2.3.
The evaluation results are shown in Table 20.
18.4 Evaluation of Fatigue Strength
With respect to the sintered bodies of the respective sample Nos. shown in Table 19, the fatigue strength was measured in the same manner as in 2.4.
Then, the measured fatigue strength was evaluated according to the evaluation criteria described in 2.4.
The evaluation results are shown in Table 20.
18.5 Evaluation of Corrosion Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 19, the corrosion resistance was measured in the same manner as in 2.5.
Then, the measured corrosion resistance was evaluated according to the evaluation criteria described in 2.5.
The evaluation results are shown in Table 20.
18.6 Evaluation of Wear Resistance
With respect to the sintered bodies of the respective sample Nos. shown in Table 19, the wear resistance was measured in the same manner as in 2.6.
Then, the measured wear resistance was evaluated according to the evaluation criteria described in 2.6.
The evaluation results are shown in Table 20.
18.7 Evaluation of Dimensional Accuracy
With respect to the sintered bodies of the respective sample Nos. shown in Table 19, the dimensional accuracy was measured in the same manner as in 2.7.
Then, the measured dimensional accuracy was evaluated according to the evaluation criteria described in 2.7.
The evaluation results are shown in Table 20.
As apparent from Table 20, it was confirmed that the sintered bodies corresponding to Example each have a higher relative density than the sintered bodies corresponding to Comparative Example. It was also confirmed that there is a significant difference in properties such as tensile strength, 0.2% proof stress, and elongation between them. Further, it was also confirmed that there is a significant difference in corrosion resistance, wear resistance, and dimensional accuracy between them.
The entire disclosure of Japanese Patent Application No. 2016-134538 filed Jul. 6, 2016 is expressly incorporated by reference herein.
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