Patent Application
20240392420
The present invention relates to an Fe-based alloy, an alloy member, a product, and a method for manufacturing the alloy member.
For hot precision press working tools such as punching tools or metal dies, hot work tool steel such as SKD8, which is regulated by JIS G 4404, with high strength at elevated temperatures, or high-speed tool steel such as SKH51, which is regulated by JIS G 4403, have been used conventionally. However, with the above materials, set-in fatigue, wearing, fracture, and heat cracks can easily occur.
For example, Japanese Unexamined Patent Application Publication No. S51-072906 (JP-A-S51-072906) discloses a high-speed tool steel that is fabricated by powder metallurgy and includes, by mass ratio, 0.8-3.95% of C, 30-50% of a total amount of W and Mo, in which the mass of Mo is twice the mass of W, 3.0-5.0% of Cr, 1.0-10.0% of V, 5-15% of Co with the remainder made up of Fe and unavoidable impurities. The high-speed tool steel disclosed in JP-A-S51-072906 includes a lot of residual carbide at the time of quenching, and the residual carbide is finely dispersed uniformly onto a base. Thus, the high-speed tool steel has high wear resistance along with high toughness, thereby having high durability against cutting.
In the high-speed tool steel of JP-A-S51-072906, since an alloy is formed by powder metallurgy, precipitation or segregation etc. of primary crystals may hardly occur compared to a common case in which molten metal is solidified, and thus a uniform structure can be easily formed both microscopically and macroscopically. In general, the uniform structure is effective for mechanical properties, and a wear resistant property can also be gained by the uniform dispersion of carbide. However, when used for metal dies or the like, adhesive wearing of slid faces thereof, in particular, may occur and thus higher wear resistance has been expected.
It is an object of the present invention to provide an Fe-based alloy having excellent mechanical properties as well as an excellent wear resistant property, an alloy member, a product, and a method for manufacturing the alloy member.
To achieve the above object, a first aspect of the present invention is an Fe-based alloy that has an alloy structure including C, Cr, W, Mo, and V, with the remainder made up of Fe and unavoidable impurities, and including a Fe—BCC phase and a W—Mo-concentrated phase. By mass, the Fe—BCC phase includes 3% or more and 7% or less of C, 2% or more and 6% or less of Cr, 0.5% or more and 8% or less of W, 3% or more and 8% or less of Mo, 2% or more and 20% or less of V, and 60% or more and 90% or less of Fe, and the W—Mo-concentrated phase includes 5% or more and 13% or less of C, 2% or more and 12% or less of Cr, 7% or more and 17% or less of W, 11% or more and 22% or less of Mo, 3% or more and 19% or less of V, and 40% or more and 50% or less of Fe. The W—Mo-concentrated phase is formed so as to surround the Fe—BCC phase.
It is preferable that the Fe-based alloy as a whole includes, by mass, 0.3% or more and 2.8% or less of C, 3.0% or more and 10.0% or less of Cr, 1.5% or more and 10.5% or less of W, 2.0% or more and 9.0% or less of Mo, 1.0% or more and 8.0% or less of V, and the remainder made up of Fe and unavoidable impurities.
It is preferable that the Fe-based alloy further includes either one of or both of Si and Mn, in which Si is included 1.0% or less by mass and Mn is included 0.1% or more and 1.0% or less by mass.
It is preferable that the Fe-based alloy as a whole further includes, by mass, 10.5% or less of Co, the Fe—BCC phase further includes 9% or more and 13% or less of Co, and the W—Mo-concentrated phase further includes 6% or more and 11% or less of Co.
It is preferable that the W—Mo-concentrated phase is formed by including a lamellar structure or substantially ring-shaped depositions.
According to the first aspect of the present invention, an alloy having excellent mechanical properties can be obtained. Also, since the alloy includes the Fe—BCC phase and the W—Mo-concentrated phase, in which the W—Mo-concentrated phase is formed so as to surround the Fe—BCC phase, the relatively softer Fe—BCC phase wears down primarily when a metal die, for example, is slid, leaving the worn parts being formed into dimple shapes. The dimple-shaped parts hold lubricant oil or the like, thereby preventing occurrence of adhesive wear. Thus, the alloy has an excellent wear resistant property.
Such the alloy can be obtained by using an additive manufacturing method (hereinafter referred as a metal additive manufacturing or, simply, an additive manufacturing), in which desirable composition of metal powder is formed into the alloy.
Also, the W—Mo-concentrated phase forms the lamellar structure or the substantially ring-shaped depositions, and thus the high mechanical properties and the wear resistant property can be obtained with more certainty.
A second aspect of the present invention is an alloy member that includes at least partly the Fe-based alloy according to the first aspect of the present invention.
It is preferable that the Fe-based alloy is formed on a surface of a base material of the alloy member, a thickness of a top layer from an interface between the base material and the Fe-based alloy to a surface of the Fe-based alloy is between 0.1 mm and 2 mm, hardness of the top layer is 700 HV or more, and an average crystal grain diameter of the Fe—BCC phase is 3.0 μm or more.
The alloy member may include any one of a nitride layer, a compound layer, and a ceramic coating layer on the surface of the Fe-based alloy.
According to the second aspect of the present invention, an alloy member having excellent mechanical properties as well as an excellent wear resistant property can be obtained.
Also, by forming an alloy layer that is made of the Fe-based alloy according to the first aspect of the present invention on the surface of the base material, a member having a wear-resistant surface can be obtained. Also, even if a part of the surface is damaged, for example, the alloy layer can be formed again by deposition on the damaged part only. Thus, repairing is easy and the alloy member having excellent mechanical properties as well as an excellent wear resistant property can be obtained.
Also, further forming the nitride layer or the like on the surface can provide higher durability.
A third aspect of the present invention is a product that includes at least partly the alloy member according to the second aspect of the present invention.
According to the third aspect of the present invention, a product having excellent mechanical properties as well as an excellent wear resistant property can be obtained.
Favorable examples of such the product are a hot stamping die, a cold forging die, and a cold pressing die.
A fourth aspect of the present invention is a method for manufacturing an alloy member. The method includes using alloy powder including, by mass, 0.3% or more and 2.8% or less of C, 3.0% or more and 10.0% or less of Cr, 1.5% or more and 10.5% or less of W, 2.0% or more and 9.0% or less of Mo, 1.0% or more and 8.0% of less of V, and the remainder made up of Fe and unavoidable impurities, forming a solidified layer by melting and solidifying the alloy powder by applying an electron beam or a laser beam onto the alloy powder, forming another solidified layer onto the solidified layer, and repeating the above steps to obtain the alloy member having a layered structure.
Also, the alloy powder may further include Co and it is preferable that the alloy powder includes 10.5% or less of Co by mass.
The method may further include a surface treatment step for performing a surface treatment on the obtained alloy member. The surface treatment step may be a film formation using a nitride treatment or a PVD method.
According to the fourth aspect of the present invention, an alloy member having excellent mechanical properties as well as an excellent wear resistant property can be obtained.
The additional surface treatment, such as forming a nitride layer on a surface, can further enhance the wear resistance of the alloy member.
The present invention can provide an Fe-based alloy having excellent mechanical properties as well as an excellent wear resistant property, an alloy member, a product, and a method for manufacturing the alloy member.
Hereinafter, an embodiment of the present invention will be described. Firstly, an Fe-based alloy will be described, and then an additive manufacturing method will be described. In the descriptions hereinafter, “%” will refer to “mass percent”. Also, in the present description, the numerical value range presented by using “−” will refer to a range that includes numerical values specified before and after “−”, representing a lower limit value and an upper limit value of the range, respectively.
An Fe-based alloy according to the present embodiment has an alloy structure including C, Cr, W, Mo, and V, with the remainder made up of Fe and unavoidable impurities, and including a Fe—BCC phase and a W—Mo-concentrated phase. By mass, the Fe—BCC phase includes 3-7% of C, 2-6% of Cr, 0.5-8% of W, 3-8% of Mo, 2-20% of V, and 60-90% of Fe, and the W—Mo-concentrated phase includes 5-13% of C, 2-12% of Cr, 7-17% of W, 11-22% of Mo, 3-19% of V, and 40-50% of Fe. The W—Mo-concentrated phase is formed so as to surround the Fe—BCC phase.
Also, it is preferable that the Fe-based alloy according to the present embodiment further includes, by mass, 10.5% or less of Co, the Fe—BCC phase includes 9% or more and 13% or less of Co, and the W—Mo-concentrated phase includes 6% or more and 11% or less of Co. Also, 3% or more and 11% or less is more preferable, and 6% or more and 10% or less of Co is further more preferable.
For the Fe-based alloy according to the present embodiment, since the W—Mo-concentrated phase is formed continuously in substantial ring shapes or the W—Mo-concentrated phase is divided but arranged in the substantial ring shapes, a structure in which the W—Mo-concentrated phase surrounds the Fe—BCC phase can be obtained. In this way, the structure is microscopically heterogeneous, that is, the structure has a distribution of W—Mo-concentrated phase and Fe—BCC phase that are not completely mixed with each other. However, when such the structure happens to be a slid face, the relatively softer Fe—BCC phase wears down primarily before the relatively harder W—Mo-concentrated phase, leaving Fe—BCC phase surrounded by the W—Mo-concentrated phase being worn down into dimple shapes. However, the dimple-shaped parts hold lubricant oil, which can improve the wear resistance. In addition, such dimple-shaped parts are formed dispersedly, thereby preventing occurrence of adhesive wear.
Also, it is preferable that the Fe-based alloy as a whole includes, by mass, 0.3% or more and 2.8% or less of C, 3.0% or more and 10.0% or less of Cr, 1.5% or more and 10.5% or less of W, 2.0% or more and 9.0% or less of Mo, 1.0% or more and 8.0% of less of V, 10.5% or less of Co, and the remainder made up of Fe and unavoidable impurities. It is also preferable that the Fe-based alloy further includes either one of or both of Si and Mn, in which Si is included 1.0% or less by mass and Mn is included 0.1% or more and 1.0% or less by mass. Si is expected to improve oxidation resistance and preferably included within the above range when taking workability into consideration. Mn is expected to have effects on improving wear resistance and quenching performance as well on reducing embrittlement. On the other hand, taking influence of the embrittlement due to quench cracks or residual y into consideration, Mn is preferably included within the above range.
For the alloy of the present embodiment, an average crystal grain diameter of the Fe—BCC phase is preferably 3.0 μm or more, or, more preferably, 5.0 μm or more. Fe—BCC phase includes Fe in the BCC phase with C, Cr, W, Mo, V, and Co being included within the above-mentioned composition range. A method for calculating the average crystal grain diameter of the Fe—BCC phase will be described below.
The W—Mo-concentrated phase is a region in which W and Mo are more concentrated than in the Fe—BCC phase. The W—Mo-concentrated phase may preferably form mesh-like lamellar structures or depositions. The mesh-like lamellar structures or the depositions include a lot of W and Mo in particular. For example, a lower limit of a total amount of W and Mo (W+Mo) is preferably 15% or more, more preferably 20% or more, or further more preferably 26% or more. Also, an upper limit of the total amount of W and Mo (W+Mo) is preferably 60.0% or less, more preferably 52.0% or less, or further more preferably 45.0% or less. Also, for example, a lower limit of a ratio of the total amount of W and Mo (W+Mo) to Fe ((W+Mo)/Fe) in the W—Mo-concentrated phase is preferably 0.25 or more, and more preferably 0.60 or more. An upper limit of the ratio of the total amount of W and Mo (W+Mo) to Fe ((W+Mo)/Fe) is preferably 2.50 or less, and more preferably 2.40 or less.
The Fe—BCC phase is formed within a region that is surrounded by the mesh-like lamellar structure or the substantially ring-shaped depositions of the W—Mo-concentrated phase. That is, the W—Mo-concentrated phase is formed continuously in substantial ring shapes so as to surround the Fe—BCC phase (and other phases). The W—Mo-concentrated phase formed continuously in the substantial ring shapes is formed into substantial ring shapes having a circle equivalent diameter of approximately 10 μm in many cases, and it is preferable that the circle equivalent diameter is between 5 μm and 20 μm.
A lower limit of the average crystal grain diameter of the Fe—BCC phase formed within the region surrounded by the W—Mo-concentrated phase is 3.0 μm, preferably 4.8 mm, and more preferably 5.0 μm. Also, although an upper limit thereof is not particularly specified, it is preferable that the upper limit is 8.0 μm or less, preferably 6.5 μm or less, and more preferably 5.5 μm or less.
The W—Mo-concentrated phase may not be completely continuous but may be divided. For example, for the alloy of the present embodiment treated with quenching treatment or quenching and tempering treatments, depositions having a grain diameter of approximately 1 μm are formed being arranged in substantial ring shapes with circle equivalent diameters of 5-20 μm.
With the quenching treatment, the W—Mo-concentrated phase is to be temporarily a solid solution with the base, and carbide forming elements such as V, W, and Mo are deposited as carbide during a cooling process or a tempering process after the quenching. The above depositions with the grain diameter of approximately 1 μm are supposed to be a carbide phase of the deposited carbide. Even in this case, the W—Mo-concentrated phase may be formed being arranged in a predetermined direction forming a substantial ring shape as a whole, instead of being uniformly distributed. Such the form is referred to as “formed so as to surround the Fe—BCC phase” or “formed in substantial ring shapes”. The region surrounded by the W—Mo-concentrated phase may include minute depositions having grain diameters of approximately 0.1-0.5 μm.
The carbide phase mentioned above is a region that includes more concentrated V, Mo, and W than in the Fe—BCC phase, with a lot of C. One example of composition of the carbide phase is, by mass, 10%-16% of C, 1%-5% of Cr, 8%-25% of W, 13%-23% of Mo, 25%-35% of V, 0%-5% of Co, and 3%-35% of Fe.
Each structure can be evaluated by using an energy-dispersive X-ray spectroscopy (EDS) and an electron back scattering diffraction (EBSD) that are attached to a scanning electron microscope (SEM). For example, as a test piece to be used for analysis, a part of the alloy is embedded within resin and then a cut face of the embedded alloy is polished for a mirror finish.
Conditions for the analysis may be, for example, an acceleration voltage of 15 kV for the SEM, a working distance between an objective lens and a top surface of an observing sample of 10 mm, and an observation magnification of 3000 times. A method for evaluating an element distribution using EDS is to obtain an element-mapping image by surface analysis on the same visual field used for the above SEM. For example, when analyzing the W—Mo-concentrated phase, targeted elements may be, for example, eight elements: C, Co, Cr, Fe, Mo, O, V, and W. The Fe—BCC phase can also be analyzed in the same way as above. A method for evaluating the phases using EBSD is to obtain a phase mapping image of a visual field of 200 μm by 200 μm with a magnification of 400 times.
The above-mentioned average crystal grain diameter of the Fe—BCC phase can be calculated as below. Firstly, the phase map obtained by EBSD (e.g., an RGB image of 200 μm by 200 μm) is sectioned according to each color (red, green, and blue) to extract Fe—BCC parts only. Noises of the image are filtered and removed, and the image is converted into a monochrome binary image, which is then black/white inverted (e.g., an originally red section (Fe—BCC phase) will be shown as black). Next, the Fe—BCC phase part is segmented by using Watershed Algorithm, and diameters of the crystal grains forming the Fe—BCC phase within the segmented view fields are calculated to find the average value. In this way, the average crystal grain diameter forming the Fe—BCC phase (the average crystal grain diameter of the Fe—BCC phase) can be calculated.
More specifically, firstly, the phase map obtained by EBSD is sectioned into a red section (Fe—BCC phase), a blue section (mainly Fe—FCC phase), and a green section (a section that is neither Fe—BCC phase nor Fe—FCC phase, which will be referred to as a “zero solution section” hereafter). From such the sectioning operation of the phase map, ratios of Fe—BCC phase and deposited carbide within the structure can be found. By converting the image of the sectioned red section into a monochrome image, the Fe—BCC phase is shown as white. By inverting such the black/white image, the blue section and the green section is then shown as white. Here, a total area is a total of areas of the red section, the blue section, and the green section, and a value found by dividing the red section (Fe—BCC phase) by the total area can be expressed as an area ratio.
The zero solution section can be shown by taking off the images of the sectioned blue section from the black/white inverted image. The zero solution section is neither Fe—BCC phase nor Fe—FCC phase, and corresponds to the deposited carbide section. Next, an average area of the deposited carbide section in the visual field is calculated, and a circle equivalent diameter of the area is then calculated to find a circle equivalent average grain diameter of the deposited carbide in the Fe—BCC phase.
Unavoidable impurities refer to very small amounts of impurities that are technically difficult to be removed. The unavoidable impurities may have been mixed into raw materials or generated due to reactions or the like with various members that come into contact with the raw materials during manufacturing processes. In a case of the alloy according to the present embodiment, specific examples of the unavoidable impurities are Al, Cu, N, Ni, O, P, S, and Ti. Among such the unavoidable impurities, P, S, O, and N are impurities that are to be restricted in particular. By mass, P is preferably 0.03% or less, S is preferably less than 0.003%, O is preferably 0.02% or less, and N is preferably 0.05% or less. Naturally, less content of such the unavoidable impurities is preferable, and 0% of the unavoidable impurities is even better.
The Fe-based alloy according to the present embodiment is manufactured by using alloy powder, forming a solidified layer by melting and solidifying the alloy powder by applying an electron beam or a laser beam onto the alloy powder, forming a new solidified layer onto the solidified layer, and repeating the above operations to obtain an additively-manufactured alloy member. That is, the alloy is manufactured using a so-called additive manufacturing method.
Here, the alloy powder is Fe-based alloy powder including the above-mentioned predetermined composition of C, Cr, W, Mo, V, and Co with the remainder made up of Fe and unavoidable impurities. Firstly, to obtain the alloy within the predetermined composition range, predetermined amounts of supply material of each of the elements are measured and are mixed together to produce raw powder. The raw powder is then used to obtain atomized powder. For example, the raw powder is loaded into a crucible and melted at high frequency. The melted alloy is dropped out of a nozzle at a bottom of the crucible, and then high-pressure Argon is sprayed to the alloy so as to produce gas-atomized powder. The gas-atomized powder is then classified to obtain the alloy powder.
The additive manufacturing method is a method for making a product by additive formation, in which fusion and solidification are repeated on individual powders. However, if a grain diameter of the alloy powder is less than 5 μm, it is difficult to obtain a volume required for one fusion-solidification, which makes it difficult to produce a decent additively-manufactured product. On the other hand, if the grain diameter of the alloy powder is more than 250 μm, the volume required for one fusion-solidification is too large, which also makes it difficult to produce a decent additively-manufactured product. Thus, the grain diameter of the alloy powder is preferably between 5 μm and 250 μm, and more preferably between 10 μm and 150 μm. Spherical powders that can be obtained from a gas-atomizing method are preferable. Also, for the grain diameters of the powders, a grain size distribution may be measured by using a laser diffraction grain size distribution measuring apparatus, for example.
For different types of additive manufacturing method, for example, the grain diameter is preferably between 10 μm and 53 μm in a selective laser melting (SLM) method; and the grain diameter is more preferably between 45 μm and 105 μm in an electron beam melting (EBM) method. Also, the grain diameter is preferably between 53 μm and 150 μm, or more preferably between 53 μm and 106 μm, in a laser metal deposition (LMD) method.
Also, in a cumulative distribution curve, which is found by a laser diffraction method and shows a relationship between the grain diameter and a cumulative volume from a side of small grain diameters, if a cumulative frequency of 50 volume % is referred to as D50, D50 is preferably 50 μm-100 μm, and more preferably 70 μm-80 μm.
As mentioned above, the Fe-based alloy powder preferably includes, by mass, 0.3-2.8% of C, 3.0-10.0% of Cr, 1.5-10.5% of W, 2.0-9.0% of Mo, 1.0-8.0% of V, and the remainder made up of Fe. It is more preferable that the Fe-based alloy powder further includes either or both of Si and Mn. If Co is included, the Fe-based alloy powder may include 10.5% or less of Co.
For example, the Fe-based alloy powder including, by mass, 0.3-2.8% of C, more than 0% and 1.0% or less of Si, 0.1-1.0% of Mn, 3.0-10.0% of Cr, 1.5-10.5% of W, 2.0-9.0% of Mo, 1.0-8.0% of V, and the remainder made up of Fe and unavoidable impurities may be used.
Also, the Fe-based alloy powder may include Co, and, in such the case, the Fe-based alloy powder including, by mass, 0.3-2.8% of C, more than 0% and 1.0% or less of Si, 0.1-1.0% of Mn, 3.0-10.0% of Cr, 1.5-10.5% of W, 2.0-9.0% of Mo, 1.0-8.0% of V, more than 0% and 10.5% or less of Co, and the remainder made up of Fe and unavoidable impurities may be used.
The composition of the alloy powder can be analyzed by using, for example, a high-frequency inductive coupling plasma (ICP) emission analysis method.
As an embodiment in which a product is fabricated through fusion and solidification by applying an electron beam or a laser beam, additive manufacturing methods for metal materials (referred to as “additive manufacturing” in the present invention), such as a powder bed fusion (PBF) method and a directed energy deposition (DED) method, are also applicable.
In the additive manufacturing, the powder delivery nozzle 3 is moved in relation to a base plate 17 (in a direction A in
The directed energy deposition method is a method for manufacturing an alloy member (a product) having a layered structure by spraying alloy powder while being moved over a base material, forming a solidified layer by melting and solidifying the alloy powder by applying an electron beam or a laser beam onto the sprayed alloy powder, forming another solidified layer onto the formed solidified layer, and repeating the above steps. More specifically, by using a three-dimensional additive manufacturing apparatus, a base plate or a surface of a product is melted rapidly by laser irradiation, raw material powder is fed into the molten pool formed by the fusion, which is then solidified by rapid cooling, and such a series of processes is repeated to produce the product. The product formed on the base plate is the Fe-based alloy according to the present embodiment. Conditions for the additive manufacturing are determined accordingly taking the grain diameter and composition of the raw powder, a size, a shape, and properties of the product, productivity, etc. into consideration. For the alloy according to the present embodiment, the conditions can be selected within the following ranges.
A thickness of one layer for the additive manufacturing is 0.1-1.0 mm or more preferably 0.4-0.5 mm, for example. A thickness of a first layer of the Fe-based alloy that is formed on a surface of a base material (the base plate) (a thickness from an interface of the base material to the surface of the first layer of the Fe-based alloy including a diffusion layer in a proximity of the interface) is 0.1-1 mm, and a total thickness from the interface of the base material to the surface of the Fe-based alloy (a thickness including the diffusion layer in the proximity of the interface) is 0.1-2 mm. A beam diameter of the laser is preferably approximately 3 mm at an emission position. A laser power is preferably 1500-2500 W. A laser scanning speed is preferably 500-1000 mm/min. An amount of powder feed is preferably 10-20 g/min.
An energy density (an energy density of a heat source: J/mm) that is to be input by the laser emission for rapid fusion of the raw material is preferably 90-300 J/mm, or more preferably within a range of 180-240 J/mm. If the energy density is too small, a defect rate may rise and, furthermore, the fed powder may not melt, which makes it harder to maintain the shape of the product. Meanwhile, if the energy density is too large, a wide range of the base plate or the product, with a center at the laser emission position, may melt, which also makes it harder to maintain the shape of the product. The energy density E (J/mm) can be found from Formula 1 using a laser power P (W) and a laser scanning speed v (mm/min).
Basically, the alloy according to the present embodiment can be used as being molded without any heat treatments. However, if the costs etc. are within permissible ranges, an additional heat treatment may be performed. For the heat treatment, either one of or both of quenching treatment and tempering treatment may be performed. Nevertheless, it is preferable to perform the tempering treatment only, without the quenching treatment at a high temperature.
Conditions for the heat treatment are, for example, in a case of the quenching treatment, holding at a temperature of 1180-1220° C. for 10-60 minutes and then cooling in oil or water. It is more preferable to cool in the oil to prevent distortion and quench cracks. Quenching and cooling using a salt bath may also be performed. The tempering treatment is a heat treatment process in which the alloy is to be kept at 400° C. or more and 700° C. or less, and, for example, the alloy is preferably maintained at a temperature of 560-580° C. for 2-6 hours and then cooled in the air.
Also, a surface treatment may be applied to the obtained alloy member. A surface treatment process for applying the surface treatment to the alloy member includes, for example, a film formation on the top surface of the Fe-based alloy using a nitride treatment or a PVD method for forming a nitride layer, a compound layer, or a ceramic coating layer. If the surface treatment is to be performed, any one or more of the nitride layer, the compound layer, and the ceramic coating layer may be chosen.
Hardness of the top layer of the alloy member can be evaluated by Vickers hardness HV (hereinafter, referred to as “the hardness”). The hardness is desirably 350 HV or more, preferably 500 HV or more, more preferably 700 HV or more, further preferably 800 HV or more, and furthermore preferably 900 HV or more. In a case without the heat treatment, 350 HV or more, or more preferably 500 HV or more can be obtained. Also, in a case with the heat treatment, 700 HV or more, more preferably 800 HV or more, and further preferably 900 HV or more can be obtained.
For a measuring method of the Vickers hardness HV, for example, an indentation load for a Vickers indenter is 0.5 kg, a retention time for indentation is 10 seconds, and the hardness is found from a length of a diagonal of an impression formed on the measuring surface due to indentation of the indenter.
Although products that include at least partly the alloy member obtained as above are not particularly limited, especially favorable examples thereof are a hot stamping die, a cold forging die, and a cold pressing die. In such cases, even if a part of a surface of a metal die, for example, is damaged, repairing is easy since the alloy layer of the present invention can be formed by deposition only on the damaged part.
The Fe-based alloy here according to the present embodiment has excellent mechanical properties as well as an excellent wear resistant property with no adhesion.
As working examples, to obtain products with aimed compositions, predetermined amounts of supply material of each of the elements are measured and are mixed together to produce raw powder. The raw powder is then loaded into a crucible and melted at high frequency in a vacuum. The melted alloy is dropped out of a nozzle of 5 mm diameter at a bottom of the crucible, and then high-pressure Argon is sprayed to the alloy so as to produce gas-atomized powder. The gas-atomized powder is then classified to obtain iron based (Fe-based) alloy powder (raw powder) of 53-106 μm and 71 μm at D50. The compositions of the obtained iron based alloy powder are shown in Table 1 and Table 2.
Next, by using a three-dimensional additive manufacturing apparatus using the directed energy deposition method (LASERTEC65 3D Hybrid, by DMG MORI Co., Ltd.), the raw powder is fed to a molten pool formed by laser emission on a base plate and melted and solidified rapidly to fabricate a product having a width of 3 mm, a length of 80 mm, and a lamination height of approximately 10 mm. The conditions for the additive manufacturing are as follows. For the base plate, maraging steel (YAG 300 by Proterial, Ltd. (YAG is a registered trademark of Proterial, Ltd.)) is used.
The conditions for the additive manufacturing are:
The products with and without heat treatments are evaluated. The heat treatments for the evaluation are: tempering only; quenching only; and tempering+quenching. The product being left as is after molding (no heat treatment) is referred to as F1, the product treated with tempering only is referred to as F2, the product treated with quenching only is referred to as F3, and the product treated with quenching and tempering is referred to as F4. For the heat treatments of the products, the product is held at 1200° C. for 0.5 hours and then cooled in oil in the quenching treatment; and the product is held at 560° C. for 4 hours and then cooled in the air in the tempering treatment. The products of the Fe-based alloy according to the present embodiment are obtained after such the heat treatments.
Each working example of the obtained Fe-based alloy products F1-F4 is observed under an SEM and EDS and evaluated. A test piece for the observation is prepared by cutting a part of the product into a small piece and embedded within resin and polishing a cut face of the embedded product to a mirror finish. An observation magnification is 3000 times. Also, an element mapping image is obtained by using an EDS on the same visual field of the SEM image with a magnification of 3000 times. The analyzed elements are eight elements: C, Co, Cr, Fe, Mo, O, V, and W.
Examples of obtained SEM images are shown in
By looking at
Although the mesh-like lamellar structures and gray-colored regions 52 that are surrounded by the W—Mo-concentrated phases can be observed, it is impossible to define that the gray-colored regions 52 are all Fe—BCC phases. Thus, the crystal grain diameter forming the Fe—BCC phase is to be calculated by the above-mentioned method.
As shown in
Also, for the product F1, minute depositions 56 having grain diameters of approximately 0.1-0.5 μm are found in the lamellar structure, i.e. the Fe—BCC phase 52 (inside a black frame in the drawing) surrounded by the W—Mo-concentrated phase. It is also found, from the element-mapping images shown in
It is found that, from the SEM images, in the product F3, which is treated with the quenching treatment after being molded, and in the product F4, which is treated with the quenching and tempering treatments after being molded, the depositions 54 having grain diameters of approximately 1 μm are arranged in ring shapes having circle equivalent diameters of 5 μm-20 μm. Similarly to the product F1, the element-mapping images for the product F3 and the product F4 are obtained, and it is found from the element-mapping images that the deposition 54 arranged in the ring shapes is the W—Mo-concentrated phase including Mo and W. Also, the minute depositions 56 having grain diameters of approximately 0.1-0.5 μm are found inside the Fe—BCC phase 52 (inside a black frame in the drawing) surrounded by the depositions 54 having grain diameters of approximately 1 μm, and it is found from the element-mapping images that such the depositions also include Mo and W.
Table 3 shows composition of each phase of the product F1 with no heat treatment. In
Also, the Fe—BCC phase mainly includes Fe and also includes Cr, W, Mo, V, Co, C, and so on within predetermined ranges. Electron diffraction patterns generated at the time of emitting electron beams to the surface of the product samples are measured by using EBSD, which can show that the Fe—BCC phase has a BCC structure.
On the other hand, Table 4 shows composition of each phase of the press-forged material F0. Similarly to the case of the product F1 with no heat treatment, in
In the press-forged material F0, although it is shown that the Fe—BCC phase has approximately the same composition as that of the working example products, the composition of the W—Mo-concentrated phase is largely different from that of the products F1-F4. That is, in the press-forged material F0, although the phase in which W and Mo are concentrated exists, the W—Mo-concentrated phase of the press-forged material F0 includes less Fe and more W and Mo than the products F1-F4. Also, looking at V that has high capability of carbide formation, the W—Mo-concentrated phase of the product F1 includes 5.2% of V, whereas the W—Mo-concentrated phase of the press-forged material F0 includes 8.2% of V, and thus the press-forged material F0 has a higher concentration of V. It is estimated from the above that carbide formation is more accelerated in the W—Mo-concentrated phase of the press-forged material F0 than in the W—Mo-concentrated phase of the product F1 with no heat treatment.
Thus, the W—Mo-concentrated phase of the press-forged material F0 is harder than the W—Mo-concentrated phase of the product F1 with no heat treatment, for example. In the press-forged material F0, from
Next, the average crystal grain diameter of the Fe—BCC phase is evaluated. The average crystal grain diameter of the Fe—BCC phase for each of F1-F4 and the press-forged material F0 is calculated by using the above method. The results are shown in Table 5. As shown in Table 5, the average crystal grain diameter of the Fe—BCC phase is 5. 28 μm for the product F1 with no heat treatment, 5.33 μm for the product F2 with the tempering treatment, 4.65 μm for the product F3 with the quenching treatment, and 4.57 μm for the product F4 with the quenching and tempering treatments. Also, the average crystal grain diameter of the Fe—BCC phase is 5.17 μm for the press-forged material F0.
In general, as a method for improving mechanical properties, a structure is to be micronized and homogenized. A press-forged material is obtained by sintering powders followed by press forging and heat treatment so as to avoid weight segregation, etc. and to obtain a uniform structure. According to such the method, as above, it is possible to obtain a structure in which the Fe—BCC phase is relatively small and the W—Mo-concentrated phase and the Fe—BCC phase are uniformly dispersed in a microscopic way.
In the present embodiment on the other hand, the W—Mo-concentrated phase is formed continuously in substantial ring shapes like a lamellar structure, or the W—Mo-concentrated phase is divided but yet arranged in substantial ring shapes. Thus, a structure in which the W—Mo-concentrated phase surrounds the Fe—BCC phase can be obtained. In this way, the structure is microscopically heterogeneous (the structure has a distribution of W—Mo-concentrated phase and Fe—BCC phase that are not completely mixed with each other). However, when such the structure happens to be a slid face, the relatively softer Fe—BCC phase wears down primarily before the relatively harder W—Mo-concentrated phase, and the Fe—BCC phase surrounded by the W—Mo-concentrated phase wears out into dimple shapes having a circle equivalent diameter of 3.0 μm or more. Thus, the dimple-shaped parts hold lubricating oil, and this can improve wear resistance. In addition, such the dimple-shaped parts are formed dispersedly, thereby preventing occurrence of adhesive wear.
The press-forged material F0, on the other hand, has high hardness as a whole as mentioned above. However, the W—Mo-concentrated phase and the Fe—BCC phase are dispersed uniformly and thus wearing progresses substantially uniformly and simultaneously as a whole. Thus, dimples or the like may not be generated, which may lead to a grease shortage and adhesion. As above, according to the present embodiment, adhesion and the like can be prevented efficiently.
Hardness of the obtained Fe-based alloy products F1-F4 is measured by using a Vickers hardness measuring device. Conditions for the measurement are: an indentation load for a Vickers indenter is 0.5 kg, a retention time for indentation is 10 seconds, and the hardness is found from a length of a diagonal of an impression formed on the measuring surface due to indentation of the indenter. The number of measurement points is 5 and an average value is calculated. Table 6 shows the results and
The product F1, which is left as is without the heat treatments after being molded, is found to have high hardness of 916 HV. This may be due to effects of the mesh-like lamellar structure. Also, it is found that the product F2 with only the tempering treatment after molding has hardness of 944 HV, the product F3 with the quenching treatment after molding has hardness of 983 HV, and the product F4 with the quenching and tempering treatments after molding has hardness of 946 HV. Although the press-forged material F0 with the quenching and tempering treatments has the highest hardness, the hardness drops to a half or less thereof if the quenching and tempering treatments are not performed onto the press-forged material. Thus, it can be said that the products have higher hardness than the press-forged material. As above, in the present embodiment, the sufficient hardness of 900 HV or more can be obtained in any of the cases, with or without the heat treatments.
As mentioned above, the product F1 and the product F2 have the mesh-like lamellar structures being formed, and are expected to have high toughness. Also, as shown in
Although the products including Co are evaluated in the working example above, Co is not always necessary. Inclusion of a predetermined amount of Co can provide high mechanical properties without heat treatments. However, in cases in which Co is not included, as will be described below in Experiment 2, sufficient mechanical properties can be obtained by performing heat treatments such as quenching.
Next, a product is fabricated by using iron-based alloy powders having an alloy composition as shown in Table 7. Similarly to Experiment 1, to obtain a product with an aimed composition, predetermined amounts of supply material of each of the elements are measured and are mixed together to produce raw powder. The raw powder is then loaded into a crucible and melted at high frequency in a vacuum. The melted alloy is dropped out of a nozzle of 5 mm diameter at a bottom of the crucible, and then high-pressure Argon is sprayed to the alloy so as to produce gas-atomized powder. The gas-atomized powder is then classified to obtain iron based (Fe-based) alloy powder of 53-106 μm and 73 μm at D50. Co is considered to be included as an unavoidable impurity.
Next, by using a three-dimensional additive manufacturing apparatus using the directed energy deposition method (LASERTEC65 3D Hybrid, by DMG MORI Co., Ltd.), the raw powder is fed to a molten pool formed by laser emission on a base plate and melted and solidified rapidly to fabricate a product having a width of 3 mm, a length of 80 mm, and a lamination height of approximately 10 mm. The conditions for the additive manufacturing are the same as in above-mentioned Experiment 1. For the base plate, maraging steel (YAG 300 by Proterial, Ltd. (YAG is a registered trademark of Proterial, Ltd.)) is used.
The products with and without heat treatments are evaluated. The heat treatments for the evaluation are: tempering only; quenching only; and tempering+quenching. The product being left as is after molding (without the heat treatments) is referred to as F11, the product treated with tempering only is referred to as F12, the product treated with quenching only is referred to as F13, and the product treated with quenching and tempering is referred to as F14. For the heat treatments of the products, similarly to the conditions in Experiment 1, the product is held at 1200° C. for 0.5 hours and then cooled in oil in the quenching treatment; and the product is held at 560° C. for 4 hours and then cooled in the air in the tempering treatment.
Each of the obtained Fe-based alloy products F11-F14 is observed under an SEM and EDS and evaluated. A test piece for the observation is prepared by cutting a part of the product into a small piece and embedded within resin, and polishing a cut face of the embedded product to a mirror finish. An observation magnification is 3000 times. Also, an element mapping image is obtained by using an EDS on the same visual field of the SEM image with a magnification of 3000 times. The analyzed elements are eight elements: C, Co, Cr, Fe, Mo, O, V, and W.
Examples of obtained SEM images are shown in
The crystal grain diameter forming the Fe—BCC phase is calculated by using the above-mentioned method. Also, as shown in
From the results of checking EDS surface analysis image, it is found that the mesh-like lamellar structure 50 includes Fe, Mo, and W, and the lamellar structure 50 can be observed as mesh-like forms since a part including a relatively low concentration of Fe element and a relatively high concentration of Mo and W elements is arranged adjacent to a part including a relatively high concentration of Fe element and a relatively low concentration of Mo and W elements. It is also found that the lamellar structure 50 is a W—Mo-concentrated phase, in which W and Mo are more concentrated than in parts other than the lamellar structure. Looking at the element mapping images shown in
As shown in
Table 8 shows composition of each phase of the product F11 as an example. In
Also, the Fe—BCC phase mainly includes Fe and also includes Cr, W, Mo, V, Co, C, and so on within predetermined ranges. Electron diffraction patterns generated at the time of emitting electron beams to the surface of the product samples are measured by using EBSD, which can show that the Fe—BCC phase is in a BCC structure.
On the other hand, Table 9 shows composition of each phase of the press-forged material F01. Similarly to the case of the product F11 with no heat treatment, in
Although it is shown that the Fe—BCC phase has approximately the same composition as that of the working example products, the composition of the W—Mo-concentrated phase of the press-forged material F01 is different from that of the products F11. In more detail, the W—Mo-concentrated phase of the press-forged material F01 includes more Fe and less W and Mo than the products F11.
Thus, the W—Mo-concentrated phase of the press-forged material F01 is harder than, for example, the W—Mo-concentrated phase of the product F11 with no heat treatment. In the press-forged material F01, from
Next, the average crystal grain diameter of the Fe—BCC phase is evaluated. The average crystal grain diameter of the Fe—BCC phase for each of F11-F14 and the press-forged material F01 is calculated by using the above method. The results are shown in Table 10. As shown in Table 10, the average crystal grain diameter of the Fe—BCC phase is 5.34 μm for the product F11 with no heat treatment, 5.18 μm for the product F12 with the tempering treatment, 5.05 μm for the product F13, and 4.84 μm for the product F14. Also, the average crystal grain diameter of the Fe—BCC phase is 4.62 μm for the press-forged material F01. Also, a ratio of the deposited carbide in F12-F14 is 0.6% or more and 2.4% or less. Also, a ratio of the Fe—BCC phase in F11-F14 is 45.0% or more, and a ratio of the deposited carbide deposited in the Fe—BCC phase is 0.5% ore more.
In general, as a method for improving mechanical properties, a structure is to be micronized and homogenized. A press-forged material is obtained by sintering powders followed by press forging and heat treatment so as to avoid weight segregation and to obtain a uniform structure. According to such the method, as above, it is possible to obtain a structure in which the Fe—BCC phase is relatively small and the W—Mo-concentrated phase and the Fe—BCC phase are uniformly dispersed in a microscopic way.
In the present embodiment on the other hand, the W—Mo-concentrated phase is formed continuously in substantial ring shapes (a lamellar structure), or the W—Mo-concentrated phase is divided but yet arranged in substantial ring shapes. Thus, a structure in which the W—Mo-concentrated phase surrounds the Fe—BCC phase can be obtained. In this way, the structure is microscopically heterogeneous (the structure has a distribution of W—Mo-concentrated phase and Fe—BCC phase that are not completely mixed with each other). However, when such the structure happens to be a slid face, the relatively softer Fe—BCC phase wears down primarily before the relatively harder W—Mo-concentrated phase, and the Fe—BCC phase surrounded by the W—Mo-concentrated phase wears out into dimple shapes having a circle equivalent diameter of 4.8 μm or more. Thus, the dimple-shaped parts hold oil, and this can improve wear resistance. In addition, such the dimple-shaped parts are formed dispersedly, thereby preventing occurrence of adhesive wear.
The press-forged material F01, on the other hand, has high hardness as a whole. However, the W—Mo-concentrated phase and the Fe—BCC phase are dispersed and thus wearing progresses substantially uniformly and simultaneously as a whole. Thus, dimples or the like many not occur, which may lead to an oil film shortage and adhesion. As above, according to the present embodiment, adhesion and the like can be prevented efficiently.
Hardness of the obtained Fe-based alloy products is measured by using a Vickers hardness measuring device. Conditions for the measurement are: an indentation load for a Vickers indenter is 0.5 kg, a retention time for indentation is 10 seconds, and the hardness is found from a length of a diagonal of an impression formed on the measuring surface due to indentation of the indenter. The number of measurement points is 5 and an average value thereof is calculated. Table 11 shows the results.
It is found that the product F11, which is left as is without the heat treatments after being molded, has hardness of 360 HV, the product F12 with only the tempering treatment after molding has hardness of 837 HV, the product F13 with the quenching treatment after molding has hardness of 804 HV, and the product F14 with the quenching and tempering treatments after molding has hardness of 748 HV.
As mentioned above, the product F11, which is left as is without the heat treatments after being molded, and the product F12, which is treated with only the tempering treatment after molding, have the mesh-like lamellar structures formed. Also, as shown in
Although the products including Co are evaluated in the working examples above, Co is not always necessary. Inclusion of Co of a predetermined amount can provide high mechanical properties without heat treatments. However, in cases in which Co is not included, sufficient mechanical properties can be obtained by performing heat treatments such as quenching.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2022-023967 | Feb 2022 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2023/005937 | 2/20/2023 | WO |
