Alloy, alloy member and product

Abstract

An alloy according to the present embodiment contains Fe, Cr and V as a first element group. Said alloy may also contain one or more types of element selected from Mn, Co, Ni, Si, Ge, Ru and Pd as a second element group. When the total is 100at% (hereinafter, written the same), the first element group each constitutes 10-45 at%, inclusive (at%=element ratio. Hereinafter, written as 10-45 at%). The Mg lattice mismatch is 13% or higher, and the dislocation movement barrier energy is 300 kJ / mol or higher.

Description

Alloys, alloy components and products

[0001] The present invention relates to an alloy, an alloy part, and a product using the same, which has resistance to alloys in a molten or plastic state, particularly magnesium alloys.

[0002] For example, JIS SKD61 is used for molds used in die casting of magnesium alloys. Repeated casting using the same mold can cause damage to the mold. The main cause of damage is erosion. It is believed that erosion occurs when the parts of the mold that come into contact with the molten magnesium alloy are alloyed, lowering the melting point. When erosion becomes severe, the eroded parts are repaired by welding to build up the damage. A preferred repair material is an alloy with a high melting point and excellent erosion resistance, including creep resistance at high temperatures. An example of such an alloy is disclosed in Patent Document 1.

[0003] In response to the demand for high strength and high corrosion resistance, high entropy alloys (HEAs) have attracted attention. For example, Patent Document 2 discloses a multi-component HEA containing titanium, zirconium, niobium, and tantalum, as well as at least one member selected from the group consisting of molybdenum, hafnium, tungsten, vanadium, and chromium. The HEA disclosed in Patent Document 2 is disclosed as being used as a metallic material for biomedical applications.

[0004] JP-T-1-502680A JP-A-2018-70949A

[0005] R. Car, M. Parrinello (1985). Unified Approach for Molecular Dynamicsand Density-Functional Theory. PHYSICAL REVIEW LETTERS. VOLUME 55, NUMBER 22,2471-2474S. J. Plimpton, E. D. Wolf (1990). Effect of interatomic potentialon simulated grain-boundary and bulk diffusion: A molecular-dynamics study.Physical Review B. VOLUME 41, NUMBER 5, 2712-2721T. Iwasaki, H. Miura (2001). Molecular dynamics analysis of adhesionstrength of interfaces between thin films. Materials Research Society. VOLUME16, NUMBER 6, 1789-1794T. Tsuru, D. C. Chrzan (2015). Effect of solute atoms on dislocationmotion in Mg: An electronic structure perspective. Scientific Reports. VOLUME 5: 8793 | DOI: 10.1038 / srep08793 ,1-8T. Iwasaki (2000). Molecular dynamics study of adhesion strength anddiffusion at interfaces between interconnect materials and underlay materials.Springer-Verlag. Computational Mechanics. VOLUME 25 (2000), 78-86Tomio IWASAKI (2018).Efficient Optimum Design of Metal with StrongAdhesion to Ceramics with a Combination of Orthogonal Array andResponse-Surface Method. Journal of the Society of Materials Science, Japan.VOLUME 67, NUMBER 8 , 803-810.

[0006] However, the alloy disclosed in Patent Document 2 does not have sufficient resistance to erosion and mechanical strength against molten magnesium alloys, etc. Therefore, an object of the present invention is to provide a multi-component alloy, an alloy member, and a manufactured product using the same that have resistance to magnesium, particularly resistance to erosion and mechanical strength, when used in processing such as casting of magnesium alloys.

[0007] Non-Patent Documents 1 to 6 disclose technical documents necessary for supplementary explanation of the embodiments of the present invention. For example, Non-Patent Document 1 describes a method for simulating the process of atomic movement based on the basic equations of quantum mechanics, i.e., the calculation principles of first-principles molecular dynamics. Since the electrons and atomic nuclei that make up atoms in a material follow the laws of quantum mechanics, the characteristics of the material can be evaluated by this simulation. Non-Patent Document 2 mentions a method for calculating diffusion coefficients using molecular dynamics simulations. Furthermore, Non-Patent Document 3 mentions a method for calculating adsorption energy using molecular dynamics simulations. Other Non-Patent Documents 4 to 6 will be mentioned in the section on modes for carrying out the invention described below.

[0008] To achieve the above-mentioned object, a first invention is an alloy characterized by containing Fe, Cr, and V as a first element group in an amount of 10 at% or more and 45 at% or less, respectively, having a lattice mismatch with Mg of 13% or more, and having a dislocation migration barrier energy of 300 kJ / mol or more.

[0009] The second element group may further include one or more elements selected from Mn, Co, Ni, Si, Ge, Ru, and Pd in ​​an amount of 10 at % or more and 25 at % or less, respectively.

[0010] In addition, the adsorption energy for Mg is 0.2 J / m ２ It is desirable that the following:

[0011] According to the first aspect of the present invention, since the lattice mismatch with magnesium is large, the alloy has excellent resistance to magnesium corrosion, and since the dislocation movement barrier energy is equal to or greater than a predetermined value, the alloy has sufficient rigidity.

[0012] Furthermore, by adding the second element group, higher resistance to Mg corrosion and mechanical properties can be obtained.

[0013] Such an effect is observed when the adsorption energy for magnesium is 0.2 J / m ２ If it is less than this, it can be obtained more reliably.

[0014] The second invention is an alloy member characterized by having at least a part thereof an alloy containing Fe, Cr, and V as a first element group in an amount of 10 at% or more and 45 at% or less, each of which is 10 at% or more and 45 at% or less, with the remainder consisting of unavoidable elements, having a lattice mismatch with Mg of 13% or more, and having a dislocation migration barrier energy of 300 kJ / mol or more.

[0015] The alloy may further contain, as a second element group, one or more elements selected from Mn, Co, Ni, Si, Ge, Ru, and Pd, each in an amount of 10 at % to 25 at %.

[0016] In addition, the adsorption energy of the alloy to Mg is 0.2 J / m ２ It is desirable that the following:

[0017] According to the second invention, since the lattice mismatch with magnesium is large, the alloy member has excellent resistance to magnesium corrosion, and since the dislocation migration barrier energy is a predetermined value or more, the alloy member has sufficient rigidity.

[0018] Furthermore, by adding the second element group, higher resistance to Mg corrosion and mechanical properties can be obtained.

[0019] In addition, the adsorption energy for magnesium is 0.2 J / m ２ If the ratio is less than this, the above effect can be obtained more reliably.

[0020] A third invention is a manufactured product at least partially including the alloy member according to the second invention.

[0021] It is also preferable that the product is a mold for processing magnesium.

[0022] According to the third aspect of the present invention, it is possible to obtain a product having excellent resistance to magnesium corrosion and sufficient rigidity, and in particular, to obtain a magnesium processing die capable of suppressing corrosion during magnesium casting or the like.

[0023] According to the present invention, it is possible to provide a multi-component alloy, an alloy part, and a product using the alloy part that have resistance to magnesium, particularly resistance to erosion and mechanical strength, during processing including casting of the magnesium alloy.

[0024] 1 shows the relationship between the adsorption energy for Mg and the short side lattice mismatch. 2 shows the Rockwell hardness (HRC) of the samples. 3 shows the structural photograph and elemental mapping of sample No. 2. 4 shows the structural photograph and elemental mapping of sample No. 13.

[0025] Hereinafter, an embodiment of the present invention will be described with reference to the accompanying drawings. In this embodiment, for example, in order to obtain resistance to molten magnesium alloys (hereinafter, sometimes simply referred to as magnesium resistance), it is necessary to make the material less susceptible to reaction with molten magnesium alloys. Therefore, the most important aspect of the resistance to reaction with molten magnesium alloys in this invention is that magnesium is less likely to be adsorbed (magnesium is less likely to approach) and to penetrate (magnesium is less likely to diffuse from the surface).

[0026] The difficulty of adsorption of magnesium is expressed by the low adsorption energy (also called peeling energy) disclosed in, for example, Non-Patent Document 5, and it can be said that the smaller the adsorption energy, the more difficult it is to adsorb. Note that the adsorption energy can be found by calculation, and the calculation method will be described later.

[0027] As shown in, for example, Non-Patent Document 6, the adsorption energy is governed by the lattice constant and its relative difference, the lattice mismatch. In other words, it can be said that the lattice constant and its relative difference, the lattice mismatch, are more dominant factors than other factors (surface energy, cohesive energy, electronegativity). For this reason, in the present invention, attention is focused on the lattice mismatch, which is the relative difference in lattice constants. It has been discovered that by using a material with a large lattice mismatch with magnesium, magnesium resistance, particularly excellent corrosion resistance, can be obtained. Note that the lattice mismatch, also called lattice mismatch, can be determined by calculation, the calculation method of which will be described later.

[0028] In the field of conventional metal materials, an example of a case where lattice mismatch has been noted is described in, for example, Non-Patent Document 5, which discusses bonding strength such as the interfacial strength between wiring films and barrier films in electronic components, and aims to reduce the lattice mismatch, ideally to zero. Contrary to these, the present invention aims to obtain magnesium resistance, i.e., the property of being less susceptible to reaction with molten magnesium, by increasing the lattice mismatch, which is the opposite of conventional thinking.

[0029] Furthermore, in order to increase resistance, it is important that dissolved magnesium does not penetrate and react from the surface. The ease of penetration of magnesium is evaluated by the diffusion coefficient from the surface to the interior. After examining the relationship between lattice mismatch and the diffusion coefficient of magnesium for several alloys, it was found that increasing the lattice mismatch can reduce the adsorption energy and the diffusion coefficient of magnesium (hereinafter simply referred to as the diffusion coefficient). The diffusion coefficient of magnesium can also be calculated, and the calculation method will be described later.

[0030] Furthermore, the less deformable an alloy is, the less likely it is to break, making it preferable. For example, in die casting, when the cycle time is shortened to increase productivity, the mold is subject to frequent high and low temperature cycles, which can easily concentrate thermal stress. For this reason, a material with high mechanical strength is preferable. Generally, the deformation of metals such as alloys is expressed by dislocation movement, and the resistance to deformation, i.e., the mechanical strength of a metal, is expressed by the resistance to dislocation movement. That is, as shown in, for example, Non-Patent Document 4, the mechanical strength of a metal is expressed by the dislocation movement barrier energy, and the higher the dislocation movement barrier energy required to move a dislocation, the more difficult it is to deform and the stronger the mechanical strength. For this reason, in the present invention, we also focused on the dislocation movement barrier energy. Details of the method for calculating the dislocation movement barrier energy will be described later.

[0031] Next, the alloy according to this embodiment will be described in more detail. FIG. 1 is a diagram showing the relationship between the lattice mismatch with magnesium (hereinafter sometimes simply referred to as lattice mismatch) and the adsorption energy of magnesium (hereinafter sometimes simply referred to as adsorption energy) for several metal elements. It can be seen from FIG. 1 that the adsorption energy decreases as the lattice mismatch increases. In particular, if the lattice mismatch is 13% or more, the adsorption energy becomes sufficiently low and no further decrease occurs. For this reason, it is desirable that the lattice mismatch be 13% or more.

[0032] On the other hand, it is difficult to obtain sufficient hardness (mechanical properties) using only an element system with a lattice mismatch of 13% or more. Therefore, we investigated ways to ensure sufficient hardness by using multiple elements to achieve a bcc structure with sufficient hardness and utilizing the effect of internal strain. As a result, we found that a multi-element alloy containing Fe, Cr, and V as the main components (Fe, Cr, and V at 50 at% or more), which has a relatively large lattice mismatch, has good properties. Table 1 shows the ranges of each component of the alloy according to this embodiment.

[0033]

[0034] The alloy according to this embodiment includes Fe, Cr, and V as the first element group. Furthermore, the alloy may further include one or more elements selected from Mn, Co, Ni, Si, Ge, Ru, and Pd as the second element group. The first element group contains 10 at% to 45 at% (at% = element ratio; hereinafter, this will be referred to as 10-45 at%) of each element when the total is 100 at% (the same applies below). Furthermore, when the alloy includes the second element group, the amount of each element in the second element group is 10 at% to 25 at%. Furthermore, when used as a mold, a high thermal conductivity is desirable to ensure a sufficient cooling rate. Therefore, B may be added to the alloy to provide a content of 1-60 at%, preferably 10-45 at%, and more preferably 14-40 at%. Furthermore, the amount of B is preferably 1.5 times or more, and more preferably 2 times or more, of the first element group or each of the first element group and the second element group.

[0035] The ranges of element ratios of the first element group and the second element group are recognized as the content of the elements constituting the high-entropy alloy. When the second element group is not included, it is more preferable that each element of the first element group be 25 to 45 at%. The element ratios of all elements constituting the alloy may be equal. The alloy according to this embodiment may contain inevitable impurities as the balance in addition to the first element group and the second element group. For example, inevitable impurity elements such as C, N, and O may each be contained at 500 ppm or less. The high-entropy alloy referred to in this specification refers to an alloy in which each element is contained at a maximum of 45 at% or less, and more preferably at a maximum of 34 at% or less.

[0036] Next, each evaluation item of the alloy according to this embodiment will be described in more detail.

[0037] [Lattice Mismatch] As described above, the alloy according to this embodiment preferably has a small adsorption energy and a small diffusion coefficient in order to prevent magnesium from approaching the surface and reacting, or from penetrating and reacting, and for this purpose, a lattice mismatch with Mg of 13% or more is required.

[0038] [Dislocation Migration Barrier Energy] Generally, the deformation of metals is expressed by the movement of dislocations, and the difficulty of deformation, i.e., the mechanical strength of a metal, is expressed by the difficulty of dislocation migration. For this reason, as shown in, for example, Non-Patent Document 4, the mechanical strength of a metal is expressed by the dislocation migration barrier energy. If this is large, for example, the hardness described below will increase. It is desirable that the alloy according to this embodiment has a dislocation migration barrier energy (for example, dislocation migration barrier energy at 800°C) of 300 kJ / mol or more. The dislocation migration barrier energy is one index that represents the mechanical strength of the alloy according to this embodiment.

[0039] [Magnesium adsorption energy] To increase resistance to molten magnesium, that is, to make it difficult to react with magnesium when it comes into contact with molten magnesium, it is important to make it difficult for magnesium to approach and difficult for magnesium to adsorb. The ease of magnesium adsorption can be evaluated by the adsorption energy mentioned above, and it can be said that the smaller the adsorption energy, the more difficult it is to adsorb. Details will be described later along with the simulation.

[0040] The alloy according to this embodiment preferably has an adsorption energy (for example, adsorption energy at 800°C) of 0.2 J / m ２ The adsorption energy can be said to be one indicator of magnesium resistance. Therefore, in this embodiment, the adsorption energy is preferably set to 0.2 J / m ２ In this embodiment, the adsorption energy is more preferably 0.15 J / m ２ or less, and more preferably 0.1 J / m ２ or less, more preferably 0.08 J / m ２ The following applies.

[0041] [Magnesium diffusion coefficient] In order to increase resistance, it is important that dissolved magnesium does not penetrate from the surface and react. The ease with which magnesium penetrates can be evaluated by the diffusion coefficient from the surface to the interior. The diffusion coefficient can be said to be one indicator of magnesium resistance. Details of the diffusion coefficient will be discussed later.

[0042] [Hardness] The alloy according to this embodiment preferably has a Vickers hardness (HV) at room temperature of at least 430. Hardness is an index that represents the mechanical strength of the alloy according to this embodiment.

[0043] [Crystal Structure] All of the alloys according to this embodiment have a body-centered cubic (bcc) crystalline structure. The crystalline structure is observed by X-ray diffraction (XRD). Note that in addition to alloys having a single type of bcc structure, alloys having multiple types of bcc structures may also be used. Furthermore, in the alloys according to this embodiment, most preferably the entire structure has a body-centered cubic lattice structure, but preferably 60% or more, more preferably 80% or more, by volume (content) of the structure has a body-centered cubic lattice structure.

[0044] Next, a method for calculating each item in this embodiment will be described. Each item can be calculated using molecular dynamics simulation as disclosed in Non-Patent Document 1, etc.

[0045] [Method of calculating lattice mismatch] The lattice constants for calculating the lattice mismatch were defined as follows based on Non-Patent Document 5. That is, the mismatch between the short-side lattice constant a and the long-side lattice constant b of a face-centered rectangular lattice representing the plane with the highest atomic number density, i.e., the close-packed crystal plane described below, was expressed in percentages, and defined as the short-side lattice mismatch Δa and the long-side lattice mismatch Δb. Since Δa, which is the shorter interatomic distance, is more important, in this embodiment, Δa is defined as the lattice mismatch unless otherwise specified.

[0046] However, in the case of SKD61 and its nitrides, which are listed in the comparative examples below, the short-side lattice mismatch Δa with magnesium is small, at approximately 2% or less, while the long-side lattice mismatch Δb is large, at 16% or more. Therefore, the arithmetic mean of Δa and Δb was used as the lattice mismatch. In the case of a body-centered cubic structure, the closest-packed crystal plane is the (110) plane, and the ratio of the short side a to the long side b is approximately 1:√2. On the other hand, the stable crystal structure of the counterpart material, magnesium, at room temperature and pressure is a hexagonal close-packed (HCP) structure, and as the temperature increases, the body-centered cubic lattice becomes stable. For example, the closest-packed crystal plane of a hexagonal close-packed structure is the (0001) plane, and the ratio of the short side a to the long side b is approximately 1:√3. It is known from non-patent document 5 and other sources that crystal planes other than the close-packed crystal planes defined here have little impact due to their weak contribution to the adsorption energy, so the determination was based on the close-packed crystal planes.

[0047] To calculate the lattice mismatch defined above, a relaxation calculation is performed using molecular dynamics simulations such as those described in Non-Patent Document 5 to determine a stable crystal structure, which allows the aforementioned a and b to be calculated, and the lattice mismatch can then be calculated based on this. The lattice constant and lattice mismatch were calculated using a self-made molecular dynamics software, and calculations were also performed in parallel using Dmol3 and Forcite in Materials Studio from Dassault Systemes, and it was confirmed that the results of both programs matched.

[0048] [Method for calculating dislocation migration barrier energy] As shown in, for example, Non-Patent Document 4, the mechanical strength of a metal is expressed by the dislocation migration barrier energy. The dislocation migration barrier energy is the barrier energy that a dislocation must overcome in the process of changing from a state before the dislocation moves to a state after the dislocation moves, and is calculated by molecular dynamics simulation, for example, in the same manner as the method shown in Non-Patent Document 4. The barrier energy was calculated using self-made molecular dynamics software, and calculations were also performed in parallel using Dmol3 and Forcite in Materials Studio by Dassault Systèmes, and it was confirmed that the results of both methods matched.

[0049] [Method for calculating adsorption energy] The adsorption energy represents the energy required to change an adsorbed state into a detached state, and can be obtained by subtracting the energy in the adsorbed state from the energy in the detached state, as shown in equation (3) in Non-Patent Document 3. The adsorption energy was calculated using a self-developed molecular dynamics software, and in parallel with calculations using Dmol3 and Forcite in Materials Studio from Dassault Systèmes, it was confirmed that the results of both were consistent. The larger this value, the easier the adsorption.

[0050] [Method of Calculating Diffusion Coefficient] As shown in equation (2) of Non-Patent Document 2, the diffusion coefficient can be calculated from the following Einstein relational equation, equation 1 (equation (A) and equation (B)).

[0051]

[0052] Equation (B) is the mean square displacement from t0 to t+t0, which is the reference time set after sufficient relaxation, divided by 6t. In reality, it converges in a finite time step, so the diffusion coefficient can be calculated without calculating up to infinity. i (t+t0)-r i (t0) can be calculated from the equation of motion. Note that the diffusion coefficient for penetration in a direction perpendicular to the interface can be calculated from the mean square displacement in that direction. The larger this diffusion coefficient, the easier it is to penetrate. In other words, this means that molten magnesium is more likely to penetrate and react from the surface, or in other words, more likely to dissolve.

[0053] [Calculation Results] Next, the alloys according to this embodiment will be described. Table 2 shows the calculation results for the lattice mismatch with Mg, dislocation migration barrier energy, and Mg adsorption energy for nine types of alloys according to this embodiment. All alloys were assumed to have equal elemental ratios. For example, when composed of three elements, the constituent elements were contained at 33.3 at% each; when composed of five elements, the constituent elements were contained at 20 at% each; and when composed of six elements, the constituent elements were contained at 16.6 at% each. Furthermore, as comparative examples, similar calculations were performed on SKD61 (JIS G 4404) alloy tool steel (for hot work dies), SKD61 surface-nitrided, and a PdRuZn alloy (equal elemental ratio). Calculation results for the diffusion coefficient, hardness, thermal conductivity, etc. of Mg in the alloys are omitted.

[0054]

[0055] Similar calculations were also performed on KUMADAI magnesium alloy (Mg—Al—Ca) (“KUMADAI magnesium alloy” is a registered trademark) as a magnesium alloy, rather than on elemental magnesium. The results are shown in Table 3.

[0056]

[0057] All alloys according to the examples have a lattice mismatch with Mg of 13% or more, a dislocation migration barrier energy of 300 kJ / mol or more, and an adsorption energy of Mg of 0.2 J / m ２ Below (0.08J / m ２ On the other hand, the conventional SKD61 alloy had a small lattice mismatch with Mg of less than 13%, and the Mg adsorption energy was 0.2 J / m, regardless of whether or not the nitriding treatment was performed. ２ Furthermore, the PdRuZn alloy, which does not contain the first element group and is mainly composed of the second element group, has a lattice mismatch with Mg of 13% or more, and the Mg adsorption energy is 0.2 J / m ２ Below (0.08J / m ２ However, the dislocation migration barrier energy is less than 300 kJ / mol, and sufficient strength cannot be obtained.

[0058] Next, additive manufacturing was actually performed on several alloys to confirm their structures, etc. As shown in Table 4, powders with alloy compositions No. 1 to No. 13 were prepared and molded using the DED (Directed Energy Deposition) method. The manufactured products are shown in Table 4. The compositions of the molded products shown in Table 4 are as follows: No. 1 and No. 2 contain 33.3 at% each of Fe, Cr, and V, which are part of the first element group. Additionally, No. 3 to No. 7, No. 14, and No. 15 contain 20 at% each of Fe, Cr, and V, which are part of the first element group, and 20 at% each of two elements selected from Mn, Co, Ni, and Si, which are part of the second element group. Additionally, No. 8 and No. 9 contain 20 at% each of Fe, Cr, and V, which are part of the first element group. No. 9 contains 20 at% each of Fe, Cr, and V, and further contains 40 at% B. No. 10 to No. 13 contain 14.3 at% each of Fe, Cr, and V of the first element group, 14.3 at% each of two elements selected from Mn, Co, Ni, and Si of the second element group, and further contains 28.6 at% B.

[0059]

[0060] Under the above conditions, for Nos. 1, 2, 8, 12, and 13, sound shaped bodies without voids were obtained.

[0061] Figure 2 shows the Rockwell hardness (HRC) of some samples. Although there are differences depending on the alloy composition, even the lowest samples generally achieved a Rockwell hardness of 37 or more (HRC = 37 or more).

[0062] As an example, Fig. 3 shows a structural photograph and elemental mapping of No. 2, and Fig. 4 shows a structural photograph and elemental mapping of No. 13. As shown in Fig. 3, in the FeCrV composition, although some segregation was observed, all elements were melted and alloyed. On the other hand, as shown in Fig. 4, in the FeCrVB composition, ２ In the CoNi composition, VB powder was added. ２ was not dissolved and was scattered in particles. ２ There was overlap in the mapping of Cr and Cr.

[0063] Next, corrosion test specimens were prepared from the shaped bodies composed of the alloy compositions of Nos. 2 and 8, and corrosion tests were conducted on Mg. The corrosion test specimens were cylindrical, with an outer diameter of φ13, an inner diameter of φ5.5, and a height of 3.5. For comparison, a similar corrosion test was also conducted on a corrosion test specimen (No. 0) made of SKD61, a hot work tool steel commonly used in Mg die casting molds, whose surface had been nitrided. The SKD61 had a Rockwell hardness of 45 HRC, and the surface had been nitrided to a thickness of 50 μm.

[0064] The prepared corrosion test specimens were placed so that they were immersed in a molten Mg alloy with a purity of 99% that had been formed in a melting furnace. The corrosion test specimens were immersed for 1 hour while stirring the Mg alloy using a stirring rod rotating at 116 revolutions per minute. The temperature of the molten metal was set to 936 K to 961 K. The corrosion test evaluated the corrosion rate. The corrosion rate was calculated by the following formula: corrosion rate [%] = (mass before test - mass after test) / mass before test x 100. The results are shown in Table 5.

[0065]

[0066] The results of the Mg corrosion test are shown in Table 5. As shown in Table 5, the corrosion rate was 0.0393% for No. 2, 0.1287% for No. 8, and 0.2778% for No. 0, a comparative example in which the surface of SKD61 was nitrided. The corrosion test results also confirmed that, compared to No. 0, which was modeled after a conventional material, alloys such as No. 2, which contain Fe, Cr, and V as part of the first element group at 10 at% to 45 at% each, and alloys such as No. 8, which contain Fe, Cr, and V as part of the first element group at 10 at% to 45 at% each and further contain B at 0.5 at% to 60 at% have superior Mg corrosion resistance.

[0067] Thus, the alloy according to this embodiment can be applied to alloy members containing the alloy at least in part (e.g., on the surface of a base material) and to manufactured products that include the alloy member in at least a portion thereof. It is particularly suitable for use in dies used in processing magnesium. For example, shaping can be performed by irradiating an alloy powder with a desired element ratio with an electron beam or laser beam, melting and solidifying it. By forming the alloy according to this embodiment on at least the surface of a magnesium die-casting die, a magnesium die-casting die that can suppress corrosion due to magnesium can be obtained.

[0068] Although the embodiments of the present invention have been described above with reference to the accompanying drawings, the technical scope of the present invention is not limited to the above-described embodiments. It is clear that those skilled in the art can conceive of various modifications and alterations within the scope of the technical ideas described in the claims, and it is understood that these modifications and alterations also fall within the technical scope of the present invention.

Claims

1. A first element group includes Fe, Cr, and V, each of which is 14.3 at% or more and 45 at% or less, The second element group further includes one or more elements selected from Mn, Co, Ni, Si, Ge, Ru, and Pd, each of which is contained in an amount of 14.3 at% or more and 25 at% or less; The balance of the alloy is unavoidable impurities.

2. The first element group contains Fe, Cr, and V in an amount of 20 at% or more and 45 at% or less, The alloy according to claim 1, characterized in that the second element group contains one or more elements selected from Mn, Co, Ni, Si, Ge, Ru, and Pd, each in an amount of 20 at% or more and 25 at% or less.

3. 3. The alloy according to claim 1, further comprising 40 at % or less of B.

4. A first element group includes Fe, Cr, and V, each of which is 10 at % or more and 45 at % or less, Contains B in an amount of 0.5 at% or more and 60 at% or less, The remainder of the alloy member is unavoidable impurities.

5. An alloy member as described in claim 4, characterized in that the second element group further contains one or more elements selected from Mn, Co, Ni, Si, Ge, Ru and Pd, each at 10 at% or more and 25 at% or less.

6. The adsorption energy for Mg is 0.2 J / m ２ 5. The alloy member according to claim 1, wherein:

7. A first element group containing Fe, Cr, and V in an amount of 14.3 at% or more and 45 at% or less, The second element group further includes one or more elements selected from Mn, Co, Ni, Si, Ge, Ru, and Pd, each of which is contained in an amount of 14.3 at% or more and 25 at% or less; The remainder of the alloy member is unavoidable impurities.

8. The first element group contains Fe, Cr, and V in an amount of 20 at% or more and 45 at% or less, The alloy member according to claim 7, characterized in that the second element group contains one or more elements selected from Mn, Co, Ni, Si, Ge, Ru, and Pd, each in an amount of 20 at% or more and 25 at% or less.

9. An alloy member according to claim 7 or claim 8, further characterized in that it contains B at 40 at% or less.

10. A first element group containing Fe, Cr, and V, each of which is 10 at% or more and 45 at% or less, Contains B in an amount of 0.5 at% or more and 60 at% or less, The remainder of the alloy member is unavoidable impurities.

11. An alloy member as described in Claim 10, characterized in that the second element group further contains one or more elements selected from Mn, Co, Ni, Si, Ge, Ru and Pd, each at 10 at% or more and 25 at% or less.

12. The alloy member according to claim 7 or 10, characterized in that the adsorption energy to Mg is 0.2 J / m 2 or less.

13. A manufactured product comprising, at least in part, the alloy member according to claim 7 or 10.

14. 14. The article of manufacture of claim 13, wherein the article of manufacture is a magnesium processing mold.