CN113046619B - Large-expansion-amount rare earth giant magnetostrictive material and preparation method thereof - Google Patents

Large-expansion-amount rare earth giant magnetostrictive material and preparation method thereof Download PDF

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CN113046619B
CN113046619B CN202110270587.8A CN202110270587A CN113046619B CN 113046619 B CN113046619 B CN 113046619B CN 202110270587 A CN202110270587 A CN 202110270587A CN 113046619 B CN113046619 B CN 113046619B
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杨鑫
陈钰凯
徐先东
黎国猛
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Abstract

The invention discloses a rare earth giant magnetostrictive material with large stretching amount and a preparation method thereof, wherein the chemical formula of the rare earth giant magnetostrictive material is as follows: tbxDy1‑xFezX is more than or equal to 0.25 and less than or equal to 0.35, and z is more than or equal to 1.92 and less than or equal to 2.00; the preparation method comprises the following steps: (i) terbium, dysprosium and iron are used as raw materials, and the materials are mixed according to the atomic ratio of each element in the rare earth giant magnetostrictive material, the burning loss rate a of the terbium and the burning loss rate b of the dysprosium; wherein the burning loss rate a of terbium is 2.5-4.7%, the burning loss rate b of dysprosium is 5.0-8.0%, and b is (1.5-2.0) x a; (ii) the prepared raw materials are smelted, directionally solidified and thermally treated to obtain the rare earth super magnetostrictive material. The invention can improve the rare earth-rich phase RFe by regulating and controlling the raw material components from the aspect of regulating and controlling the raw material proportion2Thereby improving the magnetostrictive property of the sample.

Description

Large-expansion-amount rare earth giant magnetostrictive material and preparation method thereof
Technical Field
The invention relates to a rare earth giant magnetostrictive material with large stretching amount and a preparation method thereof, belonging to rare earth magnetic functional materials.
Background
Joule (j.p. joule) discovered the magnetostrictive effect, also known as joule effect, in 1842. The magnetostrictive effect means that when a ferromagnetic material is magnetized by an external magnetic field H to change the magnetization state, the dimension L of the material is deformed by Δ L, and the amount of magnetostriction is represented by λ ═ Δ L/L. The traditional magnetostriction materials comprise materials such as Ni, Co, Fe-13% Al and the like, but the magnetostriction coefficient of the materials is 10 orders of magnitude-6～10-5Meanwhile, the application of the traditional magnetostrictive material is limited by the lower coefficient of expansion.
By the 80's of the 20 th century, research by A.E. Clark et al, the American naval surface weapon center, found that by inverting the sign of the magnetocrystalline anisotropy field, TbFe2And DyFe2The (Tb, Dy) Fe with high magnetostriction coefficient at room temperature can be obtained2A pseudo-binary alloy. This Material is called a rare earth Giant Magnetostrictive Material (GMM), which is the current MaterialThe magnetostrictive material with the largest amount of expansion is available. The room temperature magnetostriction coefficient of the material can reach 1500 ppm; has a Curie temperature of 380-420 ℃; the electromechanical coupling coefficient is more than or equal to 75 percent, and the conversion efficiency is high. Therefore, the material becomes a key component material of a plurality of advanced electronic instruments and acoustic instruments, and is widely applied to electromagnetic sensors, magnetostrictive actuators, drivers and the like of civil use, giant magnetostrictive transducers and the like of military use.
(Tb,Dy)Fe2Is made of a material having cubic MgCu2Formed of a Laves phase compound of crystal structure, which contains two asymmetric tetragonal crystal sites in the unit cell structure, so that<111>The direction in which the greatest internal distortion occurs, and therefore along the crystal<111>Directionally grown (Tb, Dy) Fe2Theoretically with the greatest amount of telescoping. Reported at present<111>The maximum expansion coefficient of the oriented single crystal giant magnetostrictive material can reach 2375ppm, but a single crystal sample is high in brittleness, a large-size product cannot be prepared, and the oriented single crystal giant magnetostrictive material has no practical application value. Therefore, the most ideal product in practical application should be<111>An oriented polycrystalline giant magnetostrictive material. However, during the preparation of the sample,<112>、<110>and<113>the direction is the easy growth direction of the crystal, resulting in<111>Oriented polycrystalline samples are difficult to prepare, on the other hand<112>Crystal orientation and<111>the included angle of (A) is 19.5 degrees,<110>crystal orientation and<111>is 35 deg., and this characteristic determines<112>And<110>the oriented polycrystalline sample also has large magnetostriction strain (the maximum can reach 1500-1650 ppm), so that the oriented polycrystalline sample is produced and applied in the market at present<112>And<110>an oriented polycrystalline giant magnetostrictive material.
The preparation method of the giant magnetostrictive material mainly adopts a directional solidification method. The directional solidification processes can be divided in particular into the Bridgman process (Bridgman), the Czochralski process (Czochralski) and the Zone melting process (Zone melting), which in turn can be divided into the horizontal and vertical Zone melting processes. US430874 published in 1981 a process for preparing rare earth giant magnetostrictive material by Bridgman method<112>Mainly oriented in the axial direction and having an alloy composition TbxDy1-xFe2-w，0<x<0.9, and w is more than or equal to 0 and less than or equal to 2.0. The Chinese patent ZL98101191.8 in 1999 discloses a chemical ingredient (Tb) which adopts raw materials1-x-yDyxRy)(Fe1-z-pBzMp)QWherein R is Ho, Er, Sm, etc., and M is Ti, V, Cr, Co, etc. x is 0.65 to 0.80, y is 0.001 to 0.1, z is 0.001 to 0.1, P is 0.001 to 0.1, and Q is 1.75 to 2.55, and the crystal is prepared by a crystal growth furnace<110>A process for preparing the axially oriented rare-earth iron giant magnetostrictive material. 2003 Chinese patent ZL02131236.2 discloses a manufacturing process of a high-temperature gradient rapid directional solidification method, and the high-temperature gradient rapid directional solidification method is prepared<113>An axially oriented giant magnetostrictive material having an alloy composition of (Tb)1-x-yDyxRy)(Fe1-z-pBezMp)QWherein R is Ho, Er, Pr, Nd, etc., and M is Ti, V, Cr, Co, etc. x is 0.65 to 0.80, y is 0.0 to 0.15, and g is 1.75 to 2.55. 2007 Chinese patent ZL200710099415.9 discloses a method for preparing a magnetic-control-type directional solidification magnetic-control-type material<111>A method for preferentially orienting a giant magnetostrictive material having the formula (Tb)1-xDyx-zNz)Fe(2+δ-y)-MyWherein M represents one or more of B, Al, Si, Ti, V and other elements, x is more than or equal to 0.45 and less than or equal to 0.75, delta is more than or equal to 0.2 and less than or equal to 0.2, y is more than or equal to 0 and less than or equal to 0.3, z is more than or equal to 0 and less than or equal to 0.2, and N represents at least one of Ce, Pr, Nd, Ho and Er. 2011 Chinese patent ZL201110331273.0 discloses a method and a device for strong magnetic field directional solidification technology, and prepares the high-intensity magnetic field directional solidification material<111>The preferred orientation giant magnetostrictive material has the mother alloy of the chemical formula (Tb)xDy1-x)FeyWherein x is more than or equal to 0.27 and less than or equal to 0.35, and y is more than or equal to 1.90 and less than or equal to 1.95. 2013, Chinese patent ZL201310443523.9 discloses a preparation process for improving magnetic property of rare earth magnetostrictive material by magnetic field heat treatment, and the raw material component of the preparation process is Tb1-x-yDyxHoyFexWherein x is 0.45-0.65, y is 0.08-0.25, and z is 1.9-2.0. In 2015, Chinese patent ZL 201510101213.8 discloses an improved directional solidification method for preparing a material with axial orientation of<110>Or<112>Method for texturing rare earth magnetostrictive rods in whichThe soil magnetostrictive rod material comprises TbmDy1-mFe2-xWherein m is more than or equal to 0.25 and less than or equal to 0.35, and x is more than or equal to 0 and less than or equal to 0.1.
The above patents relate to a material preparation process, and the axial orientation of the final sample is controlled by regulating the directional solidification process. In fact, in addition to the pull rate and temperature gradient in directional solidification, the composition of the feedstock is also a key factor in determining the final orientation effect of the sample. The raw material components are controlled in the optimal range, so that the orientation effect of the product is greatly improved. The above patent does not relate to how to adjust and optimize the sample orientation and the stretching performance from the component proportion of the raw materials and the rare earth burning loss rate. From the published patents and published papers, it is generally considered that the preferred orientations of rare earth giant magnetostrictive materials in the directional solidification process are <110> and <112>, so that the giant magnetostrictive material products produced worldwide currently mainly adopt the two methods, and if a strong magnetic field is added in the directional solidification process, polycrystalline samples mainly adopting the preferred orientation of <111> (patent ZL200710099415.9 and patent ZL201110331273.0) can be obtained, however, the processing mode has higher requirements on production equipment, the process cost is greatly increased, and the method is not suitable for industrial production.
At present, no patent technology for preparing Tb-Dy-Fe super magnetostrictive material with high elasticity and preferred orientation <111> by regulating and controlling the initial proportioning components of the alloy through calculating the rare earth burning loss rate is reported.
Disclosure of Invention
The present invention addresses the following problems: the polycrystalline giant magnetostrictive material with large expansion amount and the <111> orientation is difficult to prepare, the existing method needs to add a strong magnetic field to induce the crystal orientation in the directional solidification process, but the method has high control requirements on conditions such as air tightness, temperature gradient and the like of production equipment, has complex and difficult production process and high production cost, and is not suitable for industrial production.
In order to achieve the purpose, the chemical formula of the rare earth giant magnetostrictive material is as follows: tbxDy1-xFezX is more than or equal to 0.25 and less than or equal to 0.35, and z is more than or equal to 1.92 and less than or equal to 2.00; the preparation methodThe method comprises the following steps:
(i) terbium, dysprosium and iron are used as raw materials, and the materials are mixed according to the atomic ratio of each element in the rare earth giant magnetostrictive material, the burning loss rate a of the terbium and the burning loss rate b of the dysprosium; wherein the burning loss rate a of terbium is 2.5-4.7%, the burning loss rate b of dysprosium is 5.0-8.0%, and b is (1.5-2.0) x a;
(ii) the prepared raw materials are smelted, directionally solidified and thermally treated to obtain the rare earth super magnetostrictive material.
Preferably, a is (z/1.92) × (0.025 to 0.045) × 100%.
Preferably, in the raw materials of the step (i), the purity of terbium, dysprosium and iron is over 99.9 percent.
Preferably, in step (ii), the smelting process is as follows: placing the prepared raw materials into a vacuum arc melting furnace, and vacuumizing (for example, until the pressure in the furnace is 5X 10)-3～8×10-3Pa), then introducing argon (such as 0.4-0.8 MPa), then smelting, and obtaining a master alloy ingot after smelting.
Preferably, in the step (ii), the number of times of smelting is 4-6 times. And smelting for multiple times to ensure that the simple substance is melted and a uniform alloy is formed.
Preferably, in step (ii), the specific process of directional solidification is: removing a surface oxide layer of a smelted master alloy ingot, putting the smelted master alloy ingot into a directional solidification crystal growth furnace, controlling a crucible to descend relative to a heating area at a speed of 100-400 mm/h until the crucible moves out of the heating area, stopping the movement of the crucible, and then naturally cooling the crucible to room temperature.
Preferably, in the step (ii), the heat treatment temperature is 800-1100 ℃, and the heat treatment time is 2-24 h.
Preferably, b is 1.8 × a. Preferably, x is 0.27.
Preferably, 0.26. ltoreq. x. ltoreq.0.30. Preferably, a is 2.8% -4.0% and b is 5.0% -8.0%.
As the same inventive concept, the invention also provides a rare earth giant magnetostrictive material with large stretching amount, which is obtained by the preparation method.
Preferably, the rare earth giant magnetostrictive material is polycrystalline with <111> orientation; more preferably, the <111> crystal plane in the rare earth giant magnetostrictive material of the present invention is a preferred orientation crystal plane. Specifically, in the XRD chart, the diffraction peak of the <111> crystal plane, which is the preferred orientation, is high, and more preferably, the diffraction peak of the <111> crystal plane is highest. The XRD pattern of the polycrystal also contains diffraction peaks having other crystal plane orientations.
As can be seen from the phase diagram of TbDyFe, the Laves phase with excellent magnetostriction performance can be generated only when the raw materials are controlled in a small component interval range, and the performance of equipment, the environmental humidity and the like can influence the volatilization and oxidation of rare earth elements in the preparation process of an actual sample to cause the change of the final alloy components, so that the component proportion of the raw material alloy is reasonably adjusted to generate more rare earth-rich RFe2And the phase has great significance on the orientation and magnetostriction performance of the alloy. Through a large amount of experimental studies, this patent has successfully summarized a set of rare earth raw materials and has burnt the calculation mode of loss rate, through the ratio of regulation and control raw materials, on the basis of traditional directional solidification equipment, has prepared out the volume of big flexible<111>The oriented polycrystalline rare earth giant magnetostrictive material has simple preparation process and easy operation, and is suitable for industrial production.
The raw material components directly influence the phase composition of the material, and have important influence on the preferred orientation direction and the orientation degree in the crystal growth process. In the preparation process, the proportion of the matrix metal and the solute metal is different, and the burning loss rates of the solute metal are also different; the rare earth elements Tb and Dy are more easily volatilized in the preparation process, which can cause the occurrence of iron-rich phase RFe3Causing the final alloy composition to deviate greatly from the target value.
In order to achieve the target mixture ratio, the burning loss rate of the rare earth elements Tb and Dy, the mass calculated according to the atomic mixture ratio and the mass of each elementary substance raw material to be added are calculated according to the burning loss rate. The optimized raw material ratio is calculated in the following mode: firstly, the atomic ratio of Fe element is determined as z1Calculating the burning loss rate a of Tb on the basis: a ═ z11.92). times.cX 100 wt%, where c is 0.025,0.045]The specific value of the compound is determined according to the actual preparation processThe parameters used are adjusted, for example: when the directional solidification temperature is 1400 ℃, the pulling time is 30 minutes, and the vacuum heat treatment time is 2 hours, c can be 0.025. If the temperature of the directional solidification, the pulling time and the heat treatment time are extended, a number of more than 0.02 is required to be selected according to the actual situation, and in principle, c is preferably not more than 0.043.
According to experience, the burning loss of Dy elements is larger than that of Tb elements, the burning loss of Dy elements is about 1.1-2.0 times of that of Tb under the same preparation conditions, so the burning loss rate b of Dy is as follows: b is d × a × 100 wt%, wherein d ∈ [1.4,2.0], the specific value of d is similar to c, and the specific value also needs to be adjusted according to actual parameters, and the influencing factors are mainly solidification temperature, pulling time and heat treatment time extension.
According to the empirical formula, the burning loss rate a of terbium is 2.5-4.6%, the burning loss rate b of dysprosium is 5.0-8.0%, and the multiplying factor b/a of the burning loss rate of terbium and dysprosium is 1.4-2.0. The control of the addition amount of dysprosium to be higher than that of terbium is more favorable for generating more polycrystalline crystals with preferred orientation <111> in the target product.
Compared with the prior art, the invention has the beneficial effects that:
(1) the invention provides a calculation method of the burning loss rate of TbDyFe alloy in the directional solidification process from the aspect of regulating and controlling the raw material ratio, and the rare earth-rich phase RFe can be improved by regulating and controlling the raw material components2Thereby improving the magnetostrictive property of the sample.
(2) On the basis of the raw material proportion and the burning loss rate, the polycrystalline rare earth giant magnetostrictive material which takes <111> as the preferred growth direction of crystals and has the magnetostrictive coefficient reaching 1932ppm at room temperature is prepared by utilizing the traditional Bridgman directional solidification technology, has larger strain than <112> and <110> oriented samples, and is more beneficial to application.
(3) The preparation process and production equipment are simple and easy to operate, complex strong magnetic field technology is not required to be additionally added in the directional solidification process to induce orientation, the production cost is greatly reduced, the efficiency is high, the energy is saved, the investment is low, and the method has good industrial application prospect.
Drawings
Fig. 1 is a magnetostrictive curve of the rare earth giant magnetostrictive rod prepared in inventive example 1.
FIG. 2 is an X-ray diffraction pattern of the rare earth giant magnetostrictive rod prepared in inventive example 1.
Fig. 3 is a magnetostrictive curve of the rare earth giant magnetostrictive rod prepared in inventive example 2.
FIG. 4 is an X-ray diffraction pattern of the rare earth giant magnetostrictive rod prepared in inventive example 2.
Fig. 5 is a magnetostrictive curve of the rare earth giant magnetostrictive rod prepared in inventive example 4.
FIG. 6 is an X-ray diffraction pattern of the rare earth giant magnetostrictive rod prepared in inventive example 4.
FIG. 7 is an X-ray diffraction pattern of a rare earth giant magnetostrictive rod prepared in comparative example 3 of the present invention.
Detailed Description
The invention is described in further detail below with reference to the figures and the specific embodiments. The burn-out rate in the present invention is calculated based on mass percent, wt% represents mass percent, and at% represents atomic percent.
Example 1
Ultrasonically cleaning high-purity Tb, Dy and Fe for 30 minutes, and then carrying out ultrasonic cleaning on the Tb, Dy and Fe according to a chemical formula0.27Dy0.73Fe1.95Preparing raw materials for a target (atomic ratio); first, the burn-out rate a of Tb (1.95/1.92) × 3% to 3.05%, and the burn-out rate b of Dy (1.8 × 3.05%) to 5.49% were calculated from the atomic ratio of Fe element. According to the calculated burning loss rate, 7.9768g of terbium elementary substance, 22.3785g of dysprosium elementary substance and 19.6447g of iron elementary substance are respectively weighed, and the total weight is 50 g. Putting the raw materials into a copper crucible of a vacuum arc melting furnace, and vacuumizing the furnace to 5.5 multiplied by 10-3Pa, followed by argon to 0.6 MPa. When the formal smelting is started, firstly, the pure titanium in the smelting furnace is used for 4 times to absorb the residual oxygen in the furnace. Then, smelting of Tb-Dy-Fe master alloy is carried out, wherein each smelting lasts for 30s, and each ingot is smelted for 5 times. And after the smelting is finished, taking out the sample. Grinding the oxide layer on the surface of the melt ingot by using a grinder and abrasive paper, crushing the sample, and ultrasonically cleaningAnd washing for 20 minutes. Putting the crushed sample into a directional solidification crucible, and pumping the vacuum degree in the furnace to 8 multiplied by 10-3Pa, followed by argon. And (3) moving the sample at the temperature of 1550 ℃ at the speed of 150mm/h, and stopping moving when the sample is moved out of the heating area, so that the whole heating area is naturally cooled to room temperature. After the growth of the sample was completed, the temperature was 900 ℃ and the growth was 5X 10-3And (4) carrying out heat treatment for 2 hours under the vacuum degree of Pa to obtain a sample. The atomic ratio of the final product is Tb by energy spectrum analysis0.28Dy0.72Fe1.95The atomic ratio was substantially the same as that of the experimental setup.
A small cylinder with the diameter of 13mm multiplied by 10mm is cut for carrying out magnetostriction performance test, the magnetostriction curve under the room temperature of 14MPa is shown in figure 1, and the maximum magnetostriction coefficient under the prestress reaches 1932 ppm. The X-ray diffraction pattern of the sample is shown in fig. 2, indicating that the sample has a good <111> orientation and the crystal grain ratio of the <111> orientation is high.
Example 2
The raw material formulation and preparation method of example 2 are substantially the same as example 1 except that: the burnout rate a of the Tb element was 4.0%, and the burnout rate b of the Dy element was 7.2% for a × 1.8. The cut sample of example 2 was examined and the magnetostrictive curve at room temperature of 14MPa is shown in FIG. 3, and the maximum magnetostrictive coefficient reached 1830ppm under the prestress. The X-ray diffraction pattern of the sample is shown in fig. 4, indicating that the sample has a good <111> orientation and the crystal grain ratio of the <111> orientation is high.
Example 3
The raw material formulation and preparation method of example 3 are essentially the same as example 1, except that: the burnout rate a of the Tb element was 2.8%, and the burnout rate b of the Dy element was 5.04% for a × 1.8. The cut sample of example 3 was examined to find that the maximum magnetostriction coefficient reached 1764ppm under a prestress of 14MPa, the sample had <111> + <110> hybrid orientation and the proportion of grains having <111> orientation was the largest.
Example 4
The raw material formulation and preparation method of example 4 are essentially the same as example 1, except that: the burnout rate a of Tb element was 3.05%, and the burnout rate b of Dy element was 4.575% at a × 1.5. The cut sample of example 4 was examined, and the magnetostrictive curve at room temperature of 14MPa was shown in FIG. 5, and the maximum magnetostrictive coefficient reached 1677ppm under the prestress. The X-ray diffraction pattern of the sample is shown in fig. 6, indicating that the sample is a <110> + <111> + <112> hybrid orientation with a maximum fraction of the <110> oriented grains.
Example 5
The raw material formulation and preparation method of example 5 are essentially the same as example 1, except that: the burnout rate a of the Tb element was 3.05%, and the burnout rate b of the Dy element was 6.1% in a × 2.0. The cut sample of example 5 was tested and the maximum magnetostriction coefficient under the prestress reached 1680ppm, and the sample was also in <110> + <111> + <112> hybrid orientation, but the proportion of <111> oriented grains was slightly higher than that of <111> oriented grains of example 4.
Comparative example 1
The formulation of the raw materials and the preparation method of comparative example 1 are substantially the same as in example 1 except that: the burnout rate a of the Tb element was 2.0%, and the burnout rate b of the Dy element was 2.0% at a × 1.0. The cut samples of comparative example 1 were tested for predominantly <113> texture and had a maximum magnetostriction coefficient of only 1352ppm at 14MPa room temperature.
Comparative example 2
The formulation of the raw materials and the preparation method of comparative example 2 are substantially the same as in example 1, except that: the burnout rate a of the Tb element was 3.05%, and the burnout rate b of the Dy element was 3.05% at a × 1.0. The test was performed on a cut sample of comparative example 2, which had a <113> texture and a maximum magnetostriction coefficient of 1405ppm at 14MPa room temperature.
Comparative example 3
The formulation of the starting materials and the preparation process of comparative example 3 are essentially the same as in example 1, except that: the burnout rate a of the Tb element was 3.05%, and the burnout rate b of the Dy element was 3.66% for a × 1.2. The cut sample of comparative example 3 was examined, and the X-ray diffraction pattern of the sample is shown in FIG. 7, and the sample had a <110> + <113> + <111> hybrid texture, and the maximum magnetostriction coefficient of the sample was 1588ppm at room temperature of 14 MPa.
Comparative example 4
The formulation of the starting materials and the preparation process of comparative example 4 are essentially the same as in example 1, except that: the burning loss a of the Tb element was 5.0%, and the burning loss b of the Dy element was 5.0% at a × 1.0. The cut sample of comparative example 4 was tested for <113> + <110> hybrid texture and had a maximum magnetostriction coefficient of 1550ppm at 14MPa room temperature.
TABLE 1 summary of burn-out rates and stretch properties
Figure BDA0002974204220000071
And (4) analyzing results: the samples in the examples all stretched above 1650ppm (the accepted high level of stretching) and were predominantly in the <111> orientation, indicating that the burn-out rates in the examples are all within the optimal range. Among them, it can be seen from comparative example 1, example 2 and example 3 that the magnetostrictive performance of the sample obtained when the burning loss rate of Tb was 3.05%. It can be seen from comparison of examples 1, 4 and 5 that the best effect is obtained when the ratio of the burn-out rates of Tb and Dy is 1.8.
In comparative example 1, comparative example 2 and comparative example 3, it was found that the burn-out ratio of Tb to Dy greatly affects the material performance, indicating that these two materials have different burn-out rates, and therefore, it is necessary to set different burn-out rates. Comparative example 1, which is the worst in terms of the stretchability, was<113>Texture because the burning rate of Tb and Dy at this time is not only lower than the optimum range but also the burning rate of Dy is not higher than Tb, which results in RFe in the sample3Is too high to be advantageous for orientation. The burning loss rate of Tb in comparative example 4 was 5%, and the Tb content of the sample was necessarily greater than 0.27 at%, which resulted in a large magnetocrystalline anisotropy energy of the sample and a decrease in sample performance.

Claims (9)

1. A preparation method of a rare earth giant magnetostrictive material with large stretching amount is characterized in that the chemical formula of the rare earth giant magnetostrictive material is as follows: tbxDy1-xFezX is more than or equal to 0.25 and less than or equal to 0.35, and z is more than or equal to 1.92 and less than or equal to 2.00; the preparation method comprises the following steps:
(i) terbium, dysprosium and iron are used as raw materials, and the materials are mixed according to the atomic ratio of each element in the rare earth giant magnetostrictive material, the burning loss rate a of the terbium and the burning loss rate b of the dysprosium; wherein the burning loss rate a of terbium is 2.5-4.7%, the burning loss rate b of dysprosium is 5.0-8.0%, and b is (1.5-2.0) x a;
(ii) smelting, directionally solidifying and thermally treating the prepared raw materials to obtain a rare earth giant magnetostrictive material; the directional solidification does not need an external strong magnetic field to induce crystal orientation; the rare earth giant magnetostrictive material is polycrystal with <111> orientation.
2. The method according to claim 1, wherein a is (z/1.92) x (0.025 to 0.045) x 100%.
3. The process according to claim 1, wherein terbium, dysprosium, and iron in the starting materials of step (i) are simple substances having a purity of 99.9% or more.
4. The preparation method according to any one of claims 1 to 3, wherein in the step (ii), the smelting is carried out by the following specific processes: and putting the prepared raw materials into a vacuum arc melting furnace, vacuumizing, introducing argon, then melting, and obtaining a master alloy ingot after melting.
5. The process according to any one of claims 1 to 3, wherein in the step (ii), the number of the melting passes is 4 to 6.
6. The preparation method according to any one of claims 1 to 3, wherein in the step (ii), the specific process of directional solidification is as follows: removing a surface oxide layer of a smelted master alloy ingot, putting the smelted master alloy ingot into a directional solidification crystal growth furnace, controlling a crucible to descend relative to a heating area at a speed of 100-400 mm/h until the crucible moves out of the heating area, stopping the movement of the crucible, and then naturally cooling the crucible to room temperature.
7. The method according to any one of claims 1 to 3, wherein in the step (ii), the heat treatment temperature is 800 to 1100 ℃ and the heat treatment time is 2 to 24 hours.
8. The method according to any one of claims 1 to 3, wherein b is 1.8 x a.
9. A rare earth giant magnetostrictive material with large amount of expansion and contraction, characterized by being obtained by the production method according to any one of claims 1 to 8.
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