Mn.SUB.4.C manganese carbide magnetic substance and manufacturing method therefor

Abstract

A manganese carbide (Mn.sub.4C) magnetic material and a production method therefor are provided. According to one embodiment, the saturation magnetization of the Mn.sub.4C magnetic material increases with increasing temperature, and thus the Mn.sub.4C magnetic material is applicable to fields in which thermally induced magnetization reduction is critical.

Claims

1. A Mn.sub.4C magnetic material showing diffraction peaks of (111), (200), (220), (311) and (222) crystal planes at 2 values of 40, 48, 69, 82 and 88, respectively, in an XRD analysis.

2. The Mn.sub.4C magnetic material of claim 1, wherein the diffraction peak intensity at 2 values of 43 and 44, which correspond to impurities, is equal to or less than 2.5% of the diffraction peak intensity of the (111) crystal plane in the XRD analysis.

3. The Mn.sub.4C magnetic material of claim 1, wherein magnetization of the Mn.sub.4C magnetic material starts to increase in a temperature range of 30 K to 80 K, and the increased magnetization thereof is maintained in a temperature range of 540 K to 640 K.

4. A method for producing the Mn.sub.4C magnetic material according to claim 1, the method comprising: melting a mixture of manganese and carbon-based compound to obtain a metal mixture; cooling the melted mixture to produce an alloy ingot; and crushing the alloy ingot, and then removing impurities by magnetic separation.

5. The method of claim 4, wherein the carbon-based compound is one or more selected from graphite, graphene, carbon nanotubes, and carbon fibers.

6. The method of claim 4, wherein the mixture of manganese and carbon-based compound comprises 93 to 97 wt % of manganese and 3 to 7 wt % of the carbon-based compound.

7. The method of claim 4, wherein the melting is performed by a plasma arc melting method.

8. The method of claim 4, wherein the melting is performed at a temperature of 1,500 to 2,500 K under an inert atmosphere.

9. The method of claim 4, wherein the cooling comprises the cooling the melted mixture to a temperature of 200 K to 300 K at a rate of 10.sup.2 K/min to 10.sup.5 K/min.

10. A method for producing the Mn.sub.4C magnetic material according to claim 2, the method comprising: melting a mixture of manganese and carbon-based compound to obtain a metal mixture; cooling the melted mixture to produce an alloy ingot; and crushing the alloy ingot, and then removing impurities by magnetic separation.

11. A method for producing the Mn.sub.4C magnetic material according to claim 3, the method comprising: melting a mixture of manganese and carbon-based compound to obtain a metal mixture; cooling the melted mixture to produce an alloy ingot; and crushing the alloy ingot, and then removing impurities by magnetic separation.

Description

BRIEF DESCRIPTION OF DRAWINGS

(1) FIG. 1 is a view schematically illustrating the crystal structure of Mn.sub.4C.

(2) FIG. 2 is a view showing an X-ray diffraction pattern and an energy-dispersive X-ray spectroscopy spectrum of a Mn.sub.4C magnetic material produced according to Example 1 of the present disclosure, respectively.

(3) FIG. 3 is a graph showing the magnetization-temperature (M-T) curves of the Mn.sub.4C magnetic material, produced according to Example 1 of the present disclosure, under magnetic fields of 4 T, 1 T, and 10 mT, respectively.

(4) FIG. 4 is a graph showing the magnetic hysteresis loops of the Mn.sub.4C magnetic material, produced according to Example 1 of the present disclosure, at 4.2 K, 200 K and 400 K.

(5) FIG. 5 is an enlarged view of the temperature-dependent XRD patterns of the Mn.sub.4C magnetic material produced according to Example 1 of the present disclosure.

(6) FIG. 6 is a view showing XRD patterns after annealing the Mn.sub.4C magnetic material produced according to Example 1 of the present disclosure.

BEST MODE

(7) Hereinafter, the present disclosure will be described in detail.

(8) A Mn.sub.4C magnetic material according to one aspect of the present disclosure shows main diffraction peaks of (111), (200), (220), (311) and (222) crystal planes at 2 values of 40, 48, 69, 82 and 88, respectively, in an XRD analysis. The strong diffraction peaks of Mn.sub.4C mean that the Mn.sub.4C magnetic material is a high-purity Mn.sub.4C. For example, it may have a purity of 95% or more. Thus, according to one embodiment of the present disclosure, the diffraction peak intensity at 2 values of 43 and 44, which correspond to impurities, may be 2.5% or less, for example, 2.0% or less, of the diffraction peak intensity of the (111) crystal plane in XRD analysis.

(9) The magnetization of the Mn.sub.4C magnetic material according to one embodiment of the present disclosure may start to increase in a temperature range of 30 K to 80 K, for example, 50 K to 70 K, and the increased magnetization may be maintained in a temperature range of 540 K to 640 K, for example, 560 K to 600 K. Thus, the Mn.sub.4C magnetic material according to one embodiment of the present disclosure may maintain a stable magnetization state within the working temperature range.

(10) A method for producing a Mn.sub.4C magnetic material according to another aspect of the present disclosure includes: melting a mixture of manganese and carbon-based compound to obtain a melted mixture; cooling the melted mixture to produce an alloy ingot; and crushing the alloy ingot, and then removing impurities by magnetic separation.

(11) The manganese and carbon-based compound that are used in the method may preferably have high purity to obtain a high-purity Mn.sub.4C.

(12) The carbon-based compound may be one or more selected from graphite, graphene, carbon nanotubes, and carbon fibers.

(13) The mixture of manganese and the carbon-based compound may include 93 to 97 wt % of manganese and 3 to 7 wt % of the carbon-based compound. For example, it may include 94 to 96 wt % of manganese and 4 to 6 wt % of the carbon-based compound, or 95 to 96 wt % of manganese and 4 to 5 wt % of the carbon-based compound. When manganese and the carbon-based compound are used in amounts within the above ranges, the amount of unreacted raw materials may be reduced, and a Mn.sub.4C having a desired composition ratio may be easily produced.

(14) A melting method that is used for the melting is not particularly limited, but the melting may be performed by, for example, a plasma arc melting method.

(15) The melting may be performed at a temperature of 1,500 to 2,500 K, for example, 1,700 to 2,300 K, or 1,800 to 2,000 K, under an inert atmosphere.

(16) Thereafter, the produced melted mixture may be cooled to a temperature of 200 K to 300 K at a cooling rate of 10.sup.2 K/min to 10.sup.5 K/min, for example, 10.sup.3 K/min to 10.sup.5 K/min, or 10.sup.4 K/min to 10.sup.5 K/min, thereby producing a manganese carbide alloy ingot. A manganese carbide (Mn.sub.4C) magnetic material having a desired purity may be obtained by crushing and powdering the alloy ingot, and then magnetically separating the obtained powder to remove impurities. In this case, the crushing method is not particularly limited.

(17) The method of magnetic separation is not particularly limited, and for example, impurities may be removed several times using a magnet.

MODE FOR INVENTION

(18) Hereinafter, the present disclosure will be described in detail with reference to examples. However, the examples according to the present disclosure may be modified into various different forms, and the scope of the present disclosure is not interpreted as being limited to the examples described below. The examples of the present specification are provided to more completely explain the present disclosure to those skilled in the art.

Example 1

(19) 95 g of manganese (purity: 99.95%; purchased from Taewon Scientific Co., Ltd.) and 5 g of high-purity graphite (purity: 99.5%; purchased from Taewon Scientific Co., Ltd.) were placed in a water-cooled copper crucible of an argon plasma arc melting apparatus (manufactured by Labold AG, Germany, Model: vacuum arc melting furnace Model LK6/45), and melted at 2,000 K under an argon atmosphere. The melt was cooled to room temperature at a cooling rate of 10.sup.4 K/min to obtain an alloy ingot. The alloy ingot was crushed to a particle size of 1 mm or less by hand grinding. Thereafter, the obtained powders were magnetically separated using a Nd-based magnet to remove impurities repeatedly, and the Mn.sub.4C magnetic powders were collected. The collected Mn.sub.4C magnetic powders were subjected to X-ray diffraction (XRD) analysis (measurement system: D/MAX-2500 V/PO, Rigaku; measurement condition: CuK.sub. ray) and energy-dispersive X-ray spectroscopy (EDS) using FE-SEM (Field Emission Scanning Electron Microscope, MIRA3 LM).

(20) FIGS. 2(a) and 2 (b) show an X-ray diffraction pattern and an energy-dispersive X-ray spectroscopy graph of the Mn.sub.4C magnetic material produced according to Example 1 of the present disclosure, respectively.

(21) As can be seen in FIG. 2(a), the Mn.sub.4C magnetic material showed diffraction peaks of (111), (200), (220), (311) and (222) crystal planes at 2 values of 40, 48, 69, 82 and 88, respectively, in the XRD analysis. Thus, it can be seen that the XRD patterns of the Mn.sub.4C magnetic material produced according to Example 1 are well consistent with the patterns of the cubic perovskite Mn.sub.4C. In addition, the Mn.sub.4C magnetic material shows several very weak diffraction peaks that can correspond to Mn.sub.23C.sub.6 and Mn. That is, the diffraction peak intensity at 2 values of 43 and 44, which correspond to Mn and Mn.sub.23C.sub.6 impurities, is as very low as about 2.5% of the diffraction intensity of the peak corresponding to the (111) plane. Through this, it can be seen that the powders obtained in Example 1 have high-purity Mn.sub.4C phase. The lattice parameter of the Mn.sub.4C is estimated to be about 3.8682 .

(22) FIG. 2(b) shows the results of analyzing the atomic ratio of Mn:C in the powder by EDS. The atomic ratio of Mn:C is 80.62:19.38, which is very close to 4:1 within the experimental uncertainties. Thus, it can be seen that the powder is also confirmed to be Mn.sub.4C.

(23) The M-T curve of the field aligned Mn.sub.4C powder obtained in Example 1 was measured under an applied field of 4 T and at a temperature ranging from 50 K to 400 K. Meanwhile, the M-T curve of the randomly oriented Mn.sub.4C powder was measured under an applied field of 1 T. The Curie temperature of Mn.sub.4C was measured under 10 mT while decreasing temperature from 930 K at a rate of 20 K/min.

(24) FIGS. 3(a) to 3(c) show the M-T curves of the Mn.sub.4C magnetic material, produced according to Example 1 of the present disclosure, under magnetic fields of 4 T, 1 T, and 10 mT, respectively.

(25) FIG. 3 shows magnetization-temperature (M-T) curves indicating the results of measuring the temperature-dependent magnetization intensity of the Mn.sub.4C magnetic material, produced in Example 1, using the vibrating sample magnetometer (VSM) mode of Physical Property Measurement System (PPMS) (Quantum Design Inc.).

(26) According to the Nel theory, the ferrimagnets that contain nonequivalent substructures of magnetic ions may have a number of unusual forms of M-T curves below the Curie temperature, depending on the distribution of magnetic ions between the substructures and on the relative value of the molecular field coefficients. The anomalous M-T curves of Mn.sub.4C, as shown in FIG. 3(a), can be explained to some extent by the Nel's P-type ferrimagnetism, which appears when the sublattice with smaller moment is thermally disturbed more easily. For Mn.sub.4C with two sublattices of Mn.sub.I and Mn.sub.II, as shown in FIG. 1, the Mn.sub.I sublattice might have smaller moment.

(27) FIG. 3(a) shows the temperature dependence of magnetization of the Mn.sub.4C magnetic material produced in Example 1. The magnetization of Mn.sub.4C measured at 4.2K is 6.22 Am.sup.2/kg (4 T), corresponding to 0.258.sub.B per unit cell. The magnetization of the Mn.sub.4C magnetic material varies little at temperatures below 50 K, and is quite different from that of most magnetic materials, which undergo a magnetization deterioration with increasing temperature due to thermal agitation. Furthermore, the magnetization of the Mn.sub.4C magnetic material increases linearly with increasing temperature at temperatures above 50 K. The linear fitting of the magnetization of Mn.sub.4C at 4 T within the temperature range of 100 K to 400 K can be written as M=0.0072T+5.6788, where M and T are expressed in Am.sup.2/kg and K, respectively. Thus, the temperature coefficient of magnetization of Mn.sub.4C is estimated to be about 2.99*10.sup.4.sub.B/K per unit cell. The mechanisms of the anomalous thermomagnetic behaviors of Mn.sub.4C may be related to the magnetization competition of the two ferromagnetic sublattices (Mn.sub.I and Mn.sub.II) as shown in FIG. 1.

(28) FIG. 3(b) shows the M-T curves of the Mn.sub.4C powders at temperatures within the range of 300 K to 930 K under 1 T. The linear magnetization increment stops at 590 K, above which the magnetization of Mn.sub.4C starts to decrease slowly first and then sharply at a temperature of about 860 K. The slow magnetization decrement at temperatures above 590 K is ascribed to the decomposition of Mn.sub.4C, which is proved by further heat-treatment of Mn.sub.4C as described below.

(29) According to one embodiment of the present disclosure, the saturation magnetization of Mn.sub.4C increases linearly with increasing temperature within the range of 50 K to 590 K and remains stable at temperatures below 50 K. The increases in anomalous magnetization of Mn.sub.4C with increasing temperature can be considered in terms of the Nel's P-type ferrimagnetism. At temperatures above 590 K, the Mn.sub.4C decomposes into Mn.sub.23C.sub.6 and Mn, which are partially oxidized into the manganosite when exposed to air. The remanent magnetization of Mn.sub.4C varies little with temperature. The Curie temperature of Mn.sub.4C is about 870 K. The positive temperature coefficient (about 0.0072 Am.sup.2/kgK) of magnetization in Mn.sub.4C is potentially important in controlling the thermodynamics of magnetization in magnetic materials.

(30) The Curie temperature T.sub.e of Mn.sub.4C is measured to be about 870 K, as shown in FIG. 3(c). Therefore, the sharp magnetization decrement of Mn.sub.4C at temperatures above 860 K is ascribed to both the decomposition of Mn.sub.4C and the temperature near the Tc of Mn.sub.4C.

(31) FIG. 4 is a graph showing the magnetic hysteresis loops of the Mn.sub.4C magnetic material, produced according to Example 1 of the present disclosure, at 4.2 K, 200 K and 400 K. The magnetic hysteresis loops were measured by using the PPMS system (Quantum Design) under a magnetic field of 7 T while the temperature was changed from 4 K to 400 K.

(32) As shown in FIG. 4, the positive temperature coefficient of magnetization was further proved by the magnetic hysteresis loops of Mn.sub.4C as shown in FIG. 4. The Mn.sub.4C shows a much higher magnetization at 400 K than that at 4.2 K. Moreover, the remanent magnetization of Mn.sub.4C varies little with temperature and is 3.5 Am.sup.2/kg within the temperature range of 4.2 K to 400 K. The constant remanent magnetization of Mn.sub.4C within a wide temperature range indicates the high stability of magnetization against thermal agitation. The coercivities of Mn.sub.4C at 4.2 K, 200 K, and 400 K were 75 mT, 43 mT, and 33 mT, respectively.

(33) The magnetic properties of Mn.sub.4C measured are different from the previous theoretical results. A corner Mn.sub.I moment of 3.85.sub.B antiparallel to three face-centered Mn.sub.II moments of 1.23.sub.B in Mn.sub.4C was expected at 77 K. The net moment per unit cell was estimated to be 0.16.sub.B. In the above experiment, the net moment in pure Mn.sub.4C at 77 K is 0.26.sub.B/unit cell, which is much larger than that expected by Takei et al. It was reported that the total magnetic moment of Mn.sub.4C was calculated to be about 1.sub.B, which is almost four times larger than the 0.258.sub.B per unit cell measured at 4.2 K, as shown in FIG. 4.

(34) FIG. 5 is an enlarged view of the temperature-dependent XRD patterns of the Mn.sub.4C magnetic material produced according to Example 1 of the present disclosure.

(35) The thermomagnetic behaviors of Mn.sub.4C are related to the variation in the lattice parameters of Mn.sub.4C with temperature. It is known that the distance of near-neighbor manganese atoms plays an important role in the antiferro- or ferro-magnetic configurations of Mn atoms. Ferromagnetic coupling of Mn atoms is possible only when the MnMn distance is large enough. FIG. 5 shows the diffraction peaks of the (111) and (200) planes of Mn.sub.4C at temperatures from 16 K to 300 K. With increasing temperature, both (111) and (200) peaks of Mn.sub.4C shifted to a lower degree at temperatures between 50 K and 300 K, indicating an enlarged distance of MnMn atoms in Mn.sub.4C. No peak shift is obviously observed for Mn.sub.4C at temperatures below 50 K. The distance of nearest-neighbor manganese atoms plays an important role in the antiferro- or ferro-magnetic configurations of Mn atoms and thus has a large effect on the magnetic properties of the compounds.

(36) Thus, it can be seen that the abnormal increase in magnetization of Mn.sub.4C with increasing temperature occurs due to the variation in the lattice parameters of Mn.sub.4C with temperature.

(37) The powder produced in Example 1 was annealed in vacuum for 1 hour at each of 700 K and 923 K, and then subjected to X-ray spectroscopy, and the results thereof are shown in FIG. 6.

(38) The magnetization reduction of Mn.sub.4C at temperatures above 590 K is ascribed to the decomposition of Mn.sub.4C, which is proved by the XRD patterns of the powders after annealing Mn.sub.4C at elevated temperatures. FIG. 6 shows the structural evolution of Mn.sub.4C at elevated temperatures. When Mn.sub.4C is annealed at 700 K, a small fraction of Mn.sub.4C decomposes into a small amount of Mn.sub.23C.sub.6 and Mn. The presence of manganosite is ascribed to the spontaneous oxidation of the Mn precipitated from Mn.sub.4C when exposed to air after annealing. The fraction of Mn.sub.23C.sub.6 was enhanced significantly for Mn.sub.4C annealed at 923 K, as shown in FIG. 6.

(39) These results prove that the metastable Mn.sub.4C decomposes into stable Mn.sub.23C.sub.6 at temperatures above 590 K. The presence of Mn.sub.4C in the powder annealed at 923 K indicates a limited decomposition rate of Mn.sub.4C, from which the Tc of Mn.sub.4C can be measured. Both Mn.sub.23C.sub.6 and Mn are weak paramagnets at ambient temperature and elevated temperatures. Therefore, the magnetic transition of the Mn.sub.4C magnetic material at 870 K is ascribed to the Curie point of the ferrimagnetic Mn.sub.4C.

(40) The Mn.sub.4C shows a constant magnetization of 0.258.sub.B per unit cell below 50 K and a linear increment of magnetization with increasing temperature within the range of 50 K to 590 K, above which Mn.sub.23C.sub.6 precipitates from Mn.sub.4C. The anomalous M-T curves of Mn.sub.4C can be considered in terms of the Nel's P-type ferrimagnetism.