CN108286004B - Rare earth-nickel-aluminum material, preparation method and application thereof - Google Patents

Rare earth-nickel-aluminum material, preparation method and application thereof Download PDF

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CN108286004B
CN108286004B CN201711467029.0A CN201711467029A CN108286004B CN 108286004 B CN108286004 B CN 108286004B CN 201711467029 A CN201711467029 A CN 201711467029A CN 108286004 B CN108286004 B CN 108286004B
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姚金雷
朱宇涛
沈娇艳
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Suzhou University of Science and Technology
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C28/00—Alloys based on a metal not provided for in groups C22C5/00 - C22C27/00
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/012—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials adapted for magnetic entropy change by magnetocaloric effect, e.g. used as magnetic refrigerating material
    • H01F1/015—Metals or alloys

Abstract

The invention discloses a rare earth-nickel-aluminum material, a preparation method and application thereof. According to the formula R14Ni3Al3‑xThe raw materials are respectively weighed according to the atomic percentage and are uniformly mixed, wherein R is one of rare earth elements Gd, Tb, Dy, Ho, Er, Tm or Yb, and x is more than or equal to 0 and less than or equal to 0.3; smelting and cooling to obtain an as-cast alloy; rapidly cooling after vacuum annealing treatment to obtain a rare earth-nickel-aluminum material which is Lu14Co3In3A tetragonal crystal structure having a space group ofP42/nmc. The rare earth-nickel-aluminum material provided by the invention has large magnetic entropy change in a temperature range of 20-80K, has large magnetic refrigeration capacity, good thermal and magnetic reversible properties and low price, and is an ideal medium-temperature zone magnetic refrigeration material.

Description

Rare earth-nickel-aluminum material, preparation method and application thereof
Technical Field
The invention relates to a rare earth-nickel-aluminum material, a preparation method and application thereof, belonging to the technical field of magnetic materials.
Background
The traditional gas compression refrigeration technology is widely applied to the technical field of refrigeration and low temperature, but has the defects of low refrigeration efficiency, high energy consumption, damage to atmospheric environment and the like. The magnetic refrigeration technology is a new refrigeration technology using magnetic material as refrigeration working medium, and its refrigeration principle is by means of magnetic heat effect of magnetic refrigeration material. Under the isothermal condition, when the magnetic field intensity is increased (magnetized), the magnetic moments of the magnetic refrigeration material tend to be orderly arranged, the magnetic entropy is reduced, and heat is discharged to the outside; when the magnetization intensity is weakened (demagnetized), the magnetic moments tend to be arranged disorderly, the magnetic entropy is increased, and the magnetic refrigeration working medium absorbs heat from the outside, so that the aim of refrigeration is fulfilled. Compared with the traditional gas compression refrigeration technology, the magnetic refrigeration technology has the remarkable advantages of high efficiency, energy conservation, environmental protection, stability, reliability and the like, and is considered as a high-tech green refrigeration technology. Among them, the search for high performance magnetic refrigeration materials is the core of the practical and commercial application of magnetic refrigeration technology.
In general, the parameters for measuring the magnetocaloric properties of a magnetic refrigerant material are mainly the magnetic entropy change and the magnetic refrigeration capacity (i.e., RC, which refers to the amount of heat that can be transferred in one refrigeration cycle). The magnetic refrigeration material can be divided into low temperature (below 20K), medium temperature (20K-77K), high temperature (77K-270K) and room temperature (270K-330K) according to the working temperature regionA material. Wherein, the middle temperature zone is an important temperature zone for liquefying nitrogen, hydrogen and natural gas. At present, the research in the temperature region mainly focuses on the heavy rare earth Pr, Nd, Er, Tm and DyxEr1-xMetal and RAl2、RNi2And the like among the rare earth intermetallic compounds. However, the magnetocaloric properties of the above magnetic cooling materials are low, and the phase transition temperature range is too narrow, so that the commercial application thereof is limited. Therefore, the search for magnetic materials with reversible large magnetic entropy change and high magnetic refrigeration capacity in the medium temperature region is the key to promote the application of medium temperature magnetic refrigeration technology.
Disclosure of Invention
The invention provides a rare earth-nickel-aluminum material which has reversible large magnetic entropy change and low price and is suitable for refrigerating a medium temperature region (20K-80K), a preparation method and application thereof, aiming at the defects of the existing medium temperature magnetic refrigeration material.
The technical scheme for realizing the aim of the invention is to provide a rare earth-nickel-aluminum material with the general formula of R14Ni3Al3-xWherein R is one of rare earth elements Gd, Tb, Dy, Ho, Er, Tm or Yb, and x is more than or equal to 0 and less than or equal to 0.3.
The rare earth-nickel-aluminum material is Lu14Co3In3A tetragonal crystal structure having a space group ofP42/nmc。
The technical scheme of the invention also comprises a preparation method of the rare earth-nickel-aluminum material, which comprises the following steps:
(1) according to the formula R14Ni3Al3-xThe raw materials are respectively weighed according to the atomic percentage and are uniformly mixed, wherein R is one of rare earth elements Gd, Tb, Dy, Ho, Er, Tm or Yb, and x is more than or equal to 0 and less than or equal to 0.3;
(2) placing the raw materials mixed in the step (1) in an electric arc furnace or an induction heating furnace, vacuumizing the furnace chamber, cleaning with high-purity argon, and smelting and cooling to obtain an as-cast alloy;
(3) carrying out vacuum annealing treatment on the as-cast alloy obtained in the step (2); or induction melting and rapid quenching are carried out on the as-cast alloy obtained in the step (2) in a strip casting machine to obtain an amorphous thin strip, and then vacuum annealing treatment is carried out;
(4) quenching the alloy after the vacuum annealing treatment into liquid nitrogen or ice water for rapid cooling to obtain the rare earth-nickel-aluminum material.
In the step (1) of the technical scheme, as the rare earth element is easy to oxidize and the volatilization and burning loss of the rare earth element in the preparation process are compensated, the rare earth element raw material R is excessively added by 1-5% according to the atomic percentage, so that the single-phase material is obtained.
In the step (2), the vacuum degree of the furnace chamber is equal to or less than 5 multiplied by 10-2Pa; the smelting temperature is 1200-2000 ℃, and the smelting time is 20-100 seconds.
In the step (3), the degree of vacuum of the vacuum annealing treatment is 1X 10-3Pa～1×10-5Pa, the annealing temperature is 600-1200 ℃, and the annealing time is 1-40 days.
The technical scheme of the invention provides an application of a rare earth-nickel-aluminum material, which is used as a refrigeration material with a medium temperature zone of 20K-80K.
Compared with the prior art, the invention has the following beneficial effects:
1. the rare earth-nickel-aluminum material prepared by the invention has Lu14Co3In3The rare earth-nickel-aluminum material provided by the invention has larger magnetic entropy change and larger magnetic refrigeration capacity in a wider temperature zone (20-80K) near a medium temperature zone because the ferromagnetic-paramagnetic phase change can be changed along with the variety of rare earth elements, and Gd in the rare earth-nickel-aluminum material has larger magnetic refrigeration capacity14Ni3Al3、Dy14Ni3Al2.7The magnetic entropy change peak values respectively reach-7J/kg.K and-8J/kg.K under the change of a 0-2T magnetic field.
2. The compound provided by the invention has the advantages of good magnetic and thermal reversibility and low price, and is an ideal medium-temperature magnetic refrigeration material.
Drawings
FIG. 1 is Gd prepared according to an embodiment of the invention14Ni3Al3And Dy14Ni3Al2.7Room temperature X-ray diffraction lines of crystalline compounds;
FIG. 2 is Gd prepared according to example 1 of the present invention14Ni3Al3A thermomagnetic curve of zero field cooling and band field cooling of the crystalline compound under a 100Oe magnetic field;
FIG. 3 is Gd prepared according to example 1 of the present invention14Ni3Al3Isothermal magnetization curve of crystalline compound;
FIG. 4 is Gd prepared according to example 1 of the present invention14Ni3Al3Arrott curves for crystalline compounds;
FIG. 5 is Gd prepared according to example 1 of the present invention14Ni3Al3A plot of magnetic entropy change of a crystalline compound versus temperature;
FIG. 6 shows Dy prepared in example 2 of the present invention14Ni3Al2.7A thermomagnetic curve of zero field cooling and band field cooling of the crystalline compound under a 100Oe magnetic field;
FIG. 7 shows Dy produced in example 2 of the present invention14Ni3Al2.7Magnetic entropy change versus temperature for crystalline compounds.
Detailed Description
The technical scheme of the invention is further explained by combining the drawings and the specific embodiments.
The metal raw materials of rare earth, Ni and Al used in the following examples were purchased from Zhongnuo new materials, and the purities thereof were all higher than 99.9%. powder X-ray diffraction lines of the prepared crystalline compounds were measured by a PANALYTICAL X' Pert Pro diffractometer (Cu K α target) of Pasacaceae, Netherlands.
Example 1
This example preparation of Gd14Ni3Al3And its properties were measured.
1．Gd14Ni3Al3The preparation method specifically comprises the following steps:
step (1): according to Gd14Ni3Al3Weighing materials with chemical formula in atomic percentage, and weighing commercially available rare earth metals Gd and gold with purity higher than 99.9%Mixing Ni and Al raw materials, wherein 1% (atomic percent) of Gd is added excessively;
step (2): putting the raw materials prepared in the step (1) into an electric arc furnace or an induction heating furnace for vacuumizing until the vacuum degree reaches 5 multiplied by 10-2Pa~1×10-3When Pa, cleaning with high-purity argon with the purity of 99.999 percent for 1-2 times, and vacuumizing to 5 multiplied by 10-2Pa~1×10-3When Pa is needed, filling high-purity argon for protection, repeatedly turning and smelting for 2-3 times at the pressure of 1 atmosphere in the furnace chamber, wherein the smelting time is 20 seconds each time, and the smelting temperature is 1200-2000 ℃;
and (3): cooling in a copper crucible to obtain an as-cast alloy, wrapping the as-cast alloy with tantalum foil, and sealing in a vacuum degree of 1 × 10-3Annealing at 600 deg.C for 40 days in Pa quartz tube, taking out, rapidly quenching in liquid nitrogen to obtain Gd product14Ni3Al3A crystalline compound.
2．Gd14Ni3Al3Performance measurement of
(1) X-ray diffraction lines
See FIG. 1 for Gd measured using a PANalytical X' Pert Pro diffractometer14Ni3Al3The analysis of the powder X-ray diffraction spectrum of (1) shows that Gd is present14Ni3Al3The crystal structure is tetragonal Lu14Co3In3Type, space group isP42/nmcUnit cell parameters a = b =0.96693(7) nm, c =2.2435(2) nm, V =2.0976(2) nm3。
(2) Thermomagnetic curve
Gd determined on PPMS-Dynacool System14Ni3Al3Thermomagnetic (M-T) curves of crystalline compounds at field strength H =100Oe, as shown in fig. 2. Gd can be determined from the zero field cooling M-T curve14Ni3Al3Curie temperature T of crystalline compoundCIs 60K. In addition, the thermomagnetic curves of zero field cooling and band field cooling are completely overlapped near the Curie temperature, which shows that the ferromagnetic-paramagnetic phase of the material is changed into the second-order phase change, and the material has good thermal reversibility.
(3) Isothermal magnetization curve and Arrott curve
FIG. 3 is Gd14Ni3Al3Isothermal magnetization curves of the crystalline compound at the rising and falling fields around the curie temperature (temperature range 32K to 82K). No magnetic hysteresis was observed in the figure, which illustrates Gd obtained in this example14Ni3Al3The magnetic cooling capacity is reversible to the magnetic field.
An Arrott curve can be obtained based on the isothermal magnetization curve of FIG. 3, as shown in FIG. 4. The phase change properties of a compound can be determined by the shape of its Arrott curve, which is generally negative or sigmoidal in slope for first-order phase change materials near the phase change temperature, and positive in slope for second-order phase change materials near the phase change temperature. As can be seen from FIG. 4, the Curie temperature TCThe adjacent curves all show a positive slope, indicating that Gd was obtained in example 114Ni3Al3The ferromagnetic-paramagnetic phase of the crystalline compound changes to a typical second order phase transition around the curie temperature. The two-stage phase change material known to those skilled in the art has good magnetic and thermal reversibility and wide magnetic entropy change peak, and is beneficial to the application of the two-stage phase change material in a magnetic refrigerator.
(4) Magnetic entropy change effect and magnetic refrigeration capacity
Based on the results of fig. 3, according to maxwell's relationship:
Figure DEST_PATH_IMAGE002
from this temperature magnetization curve, the magnetic entropy change can be calculated. Gd is obtained by calculation14Ni3Al3At TCThe nearby magnetic entropy changes versus temperature (| Δ S | -T) as shown in fig. 5. As can be seen from the figure, the compound is represented by formula TCLarge magnetic entropy change appears nearby, wherein Gd is generated under the change of 0-5T magnetic field14Ni3Al3The maximum magnetic entropy changes of the crystalline compounds were-13.7J/kg K, respectively. Since a 2T magnetic field can be easily obtained by using the permanent magnet NdFeB, the magnetic entropy of the material is focused under the change of the 0-2T magnetic field. Gd under the change of 0-2T magnetic field14Ni3Al3The peak value of entropy change of the crystalline compound reaches-7J/kg.K.
The cooling capacity (RC) is another important parameter for measuring the practical value of a material. Generally, the size is the product of the peak value of the magnetic entropy change and the full width at half maximum of the entropy change-temperature curve. As can be seen from FIG. 6, under the change of 0-5T magnetic field, the peak value of entropy change reaches-13.7J/kg.K, the full width at half maximum is 70K, Gd14Ni3Al3The RC of the crystalline compound reaches 959J/kg; under the change of a 0-2T magnetic field, the entropy change peak value reaches-7J/kg.K, the full width at half maximum is 45K, and the RC reaches 315J/kg. Gd (Gd)14Ni3Al3The crystalline compound exhibits excellent magnetocaloric properties and is inexpensive.
Example 2
This example preparation of Dy14Ni3Al2.7And the properties thereof were measured.
1．Dy14Ni3Al2.7The preparation method specifically comprises the following steps:
step (1): according to Dy14Ni3Al2.7Weighing materials according to a chemical formula (namely atomic ratio), mixing commercially available Dy, Ni and Al raw materials with the purity higher than 99.9%, wherein Ni is added in an excessive amount of 5% (atomic percentage);
step (2): putting the raw materials prepared in the step (1) into an electric arc furnace or an induction heating furnace for vacuumizing until the vacuum degree reaches 5 multiplied by 10-2Pa~1×10-3When Pa, cleaning with high-purity argon with the purity of 99.999 percent for 1-2 times, and vacuumizing to 5 multiplied by 10-2Pa~1×10-3When Pa is needed, high-purity argon is filled for protection, the air pressure in the furnace chamber is 1 atmosphere, the smelting time is 100 seconds, and the smelting temperature is between 1200 and 2000 ℃;
and (3): the cast alloy is coarsely crushed and placed in the center of an induction coil in a cavity of a strip casting machine, and an amorphous thin strip sample is obtained by utilizing a vacuum melt rapid quenching method. The thin strip sample is sealed in a vacuum degree of 1X 10-3And (3) annealing the quartz tube of Pa at 600 ℃ for 1 day, taking out the quartz tube, and quickly quenching the quartz tube into ice water to obtain a crystalline compound product. Cooling in a copper crucible to obtain an as-cast alloy, wrapping the as-cast alloy with tantalum foil, and sealing in a vacuum degree of 1 × 10-5Annealing at 1200 deg.C for 1 day in Pa quartz tube, taking out, and rapidly quenching into iceIn water to obtain the product Dy14Ni3Al2.7A crystalline compound.
2．Dy14Ni3Al2.7Performance measurement of
(1) X-ray diffraction lines
Dy obtained by utilizing PANalytical X' Pert Pro diffractometer14Ni3Al2.7The room temperature X-ray diffraction line of the crystalline compound is shown in fig. 1. The results show that the structure of the product is tetragonal Lu14Co3In3Type, its space group isP42/nmcUnit cell parameters a = b =0.95044(8) nm, c =2.2795(2) nm, V =2.0596(2) nm3。
(2) Thermomagnetic curve
Dy determined on magnetic measurement system14Ni3Al2.7Thermomagnetic (M-T) curves of crystalline compounds at field strength H =100Oe, as shown in fig. 6. Dy can be determined from zero field cooling M-T curve14Ni3Al2.7Curie temperature T of crystalline compoundCIs 25K. In addition, the thermomagnetic curves of zero field cooling and band field cooling are completely overlapped near the Curie temperature, which shows that the ferromagnetic-paramagnetic phase of the material is changed into the second-order phase change, and the material has good thermal reversibility.
(3) Magnetic entropy change effect and magnetic refrigeration capacity
Dy is obtained by calculation14Ni3Al2.7At TCThe nearby magnetic entropy changes versus temperature (| Δ S | -T) as shown in fig. 7. As can be seen from the figure, the compound is represented by formula TCLarge magnetic entropy change appears nearby, wherein Dy is changed under the condition of 0-5T magnetic field14Ni3Al2.7The maximum magnetic entropy changes of the crystalline compounds were-15.7J/kg K, respectively. Dy under the change of 0-2T magnetic field14Ni3Al2.7The peak value of entropy change of the crystalline compound reaches-8J/kg.K, the full width at half maximum is 52K, and the RC of the crystalline compound reaches 416J/kg.
In the above examples, only the case where R is Gd or Dy is exemplified, but according to the present invention, R may be any of rare earth elements such as Tb, Ho, Er, Tm, and Yb, and these materials can also achieve the same or equivalent effects as in the above examples.

Claims (5)

1. A rare earth-nickel-aluminum material characterized by: it has the general formula R14Ni3Al3-xWherein R is one of rare earth elements Gd, Tb, Dy, Ho, Er, Tm or Yb, and x is more than or equal to 0 and less than or equal to 0.3; it is Lu14Co3In3A tetragonal crystal structure having a space group ofP42/nmc(ii) a The preparation method comprises the following steps:
(1) according to the formula R14Ni3Al3-xThe raw materials are respectively weighed according to the atomic percentage and are uniformly mixed, wherein R is one of rare earth elements Gd, Tb, Dy, Ho, Er, Tm or Yb, and x is more than or equal to 0 and less than or equal to 0.3; the rare earth element raw material R is added in excess by 1-5% according to atomic percentage to stabilize Lu14Co3In3A type structure;
(2) placing the raw materials mixed in the step (1) in an electric arc furnace or an induction heating furnace, vacuumizing the furnace chamber, cleaning with high-purity argon, and smelting and cooling to obtain an as-cast alloy;
(3) carrying out vacuum annealing treatment on the as-cast alloy obtained in the step (2); or induction melting and rapid quenching are carried out on the as-cast alloy obtained in the step (2) in a strip casting machine to obtain an amorphous thin strip, and then vacuum annealing treatment is carried out;
(4) quenching the alloy after the vacuum annealing treatment into liquid nitrogen or ice water for rapid cooling to obtain the rare earth-nickel-aluminum material.
2. The method for preparing a rare earth-nickel-aluminum material as set forth in claim 1, which comprises the steps of:
(1) according to the formula R14Ni3Al3-xThe raw materials are respectively weighed according to the atomic percentage and are uniformly mixed, wherein R is one of rare earth elements Gd, Tb, Dy, Ho, Er, Tm or Yb, and x is more than or equal to 0 and less than or equal to 0.3; the rare earth element raw material R is added in excess by 1-5% according to atomic percentage to stabilize Lu14Co3In3A type structure;
(2) placing the raw materials mixed in the step (1) in an electric arc furnace or an induction heating furnace, vacuumizing the furnace chamber, cleaning with high-purity argon, and smelting and cooling to obtain an as-cast alloy;
(3) carrying out vacuum annealing treatment on the as-cast alloy obtained in the step (2); or induction melting and rapid quenching are carried out on the as-cast alloy obtained in the step (2) in a strip casting machine to obtain an amorphous thin strip, and then vacuum annealing treatment is carried out;
(4) quenching the alloy after the vacuum annealing treatment into liquid nitrogen or ice water for rapid cooling to obtain the rare earth-nickel-aluminum material.
3. The method for preparing a rare earth-nickel-aluminum material according to claim 2, characterized in that: in the step (2), the vacuum degree of the furnace chamber is equal to or less than 5 multiplied by 10-2Pa; the smelting temperature is 1200-2000 ℃, and the smelting time is 20-100 seconds.
4. The method for preparing a rare earth-nickel-aluminum material according to claim 2, characterized in that: in the step (3), the degree of vacuum of the vacuum annealing treatment is 1X 10-3Pa～1×10-5Pa, the annealing temperature is 600-1200 ℃, and the annealing time is 1-40 days.
5. The use of the rare earth-nickel-aluminum material as set forth in claim 1, characterized in that it is used as a refrigerating material in the medium temperature region of 20K to 80K.
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