CN109702157B - Amorphous alloy density regulating and controlling method - Google Patents
Amorphous alloy density regulating and controlling method Download PDFInfo
- Publication number
- CN109702157B CN109702157B CN201910153140.5A CN201910153140A CN109702157B CN 109702157 B CN109702157 B CN 109702157B CN 201910153140 A CN201910153140 A CN 201910153140A CN 109702157 B CN109702157 B CN 109702157B
- Authority
- CN
- China
- Prior art keywords
- alloy
- melt
- amorphous
- amorphous alloy
- density
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Images
Abstract
The invention discloses a method for regulating and controlling the density of an amorphous alloy, which comprises the following steps: calculating the average atomic coordination number of the amorphous alloy melt: calculating the average atomic coordination number of the amorphous alloy melt at different temperatures to obtain a calculation result of the average atomic coordination number along with the temperature change; carrying out overheating treatment on the alloy melt: selecting a required average atomic coordination number according to the calculation result, determining the temperature corresponding to the selected average atomic coordination number as the overheating treatment temperature of the alloy melt, and preserving the heat of the alloy melt at the overheating treatment temperature to obtain the alloy melt after overheating treatment; a rapid solidification step: and rapidly solidifying the amorphous alloy melt after the overheating treatment to obtain the amorphous solid alloy. The invention provides a new idea and a new method for designing and preparing the microstructure of the amorphous alloy, and has the characteristics of simple and convenient implementation, high efficiency, low cost, strong controllability and repeatability, high technical reliability and the like.
Description
Technical Field
The invention relates to the technical field of preparation of metal functional materials, in particular to a method for regulating and controlling the density of an amorphous alloy.
Background
The alloy melt contains a large number of clusters of atoms of very small size, which are made up of a central atom and some of the nearest neighbors around the central atom, and therefore the structural characteristics of the clusters depend on how many of the nearest neighbors surround the central atom. The number of neighboring atoms around a central atom is conventionally referred to as the coordination number, and as the coordination number changes, both the geometric size and the geometric shape of the atom cluster change, and the change of the atom cluster structure with the coordination number is characterized in that the larger the coordination number, the higher the geometric symmetry of the atom cluster, and the geometric size increases accordingly. With the increase of the geometric symmetry of the atom clusters, the atoms in the atom clusters are arranged more closely, so that the atom clusters with different coordination numbers correspond to different atom space packing densities, the increase of the coordination numbers leads to the increase of the atom space packing densities of the atom clusters, and the density of the alloy melt is improved. The amorphous solid alloy obtained by supercooling and solidifying the melt in a high-speed cooling mode retains the atom cluster structural characteristics of the melt, because atoms cannot diffuse and rearrange to form a long-range ordered crystal structure in the quenching and solidifying process of the alloy melt, and only the long-range disordered short-range ordered atom cluster structure of the alloy melt is retained in the solid alloy, the atom cluster is a basic unit for forming the amorphous alloy. As a basic structural unit of the alloy melt, the atomic cluster structure type determines the density of the alloy melt. Because the density of the alloy melt changes little with the temperature in the process of quenching solidification, the atom cluster structure type of the alloy melt is also a key factor for determining the density of the amorphous solid alloy. In the case of a certain alloy composition, the larger the coordination number of the atomic cluster, the larger the density of the amorphous solid alloy. The atom cluster structure determines the density of the amorphous solid alloy and also determines the local electronic band structure of the amorphous solid alloy, so that the density of the amorphous solid alloy is closely related to the local electronic band structure, and the amorphous solid alloys with different densities correspond to different local electronic band structures. Since the macroscopic properties of the amorphous alloy depend on the electronic band structure, when the density of the amorphous solid alloy changes, the macroscopic properties of the amorphous solid alloy inevitably change correspondingly, so that the regulation and control of the density of the amorphous solid alloy is an effective way for optimizing the macroscopic properties of the amorphous solid alloy.
The alloy melt density is not only related to the alloy components, but also closely related to the atom cluster structure. Although the density of the amorphous solid alloy is closely related to the macroscopic performance of the amorphous solid alloy, and is one of effective ways for realizing the regulation and control of the macroscopic performance of the amorphous solid alloy, no experimental technical method is available at present for directly regulating and controlling the density of the alloy melt due to the particularity of the alloy melt, and further the regulation and control of the macroscopic performance by utilizing the density of the amorphous solid alloy is realized.
Disclosure of Invention
Aiming at the limitations of the prior art, the invention aims to provide a method for regulating and controlling the density of an amorphous alloy. The invention can regulate and control the density of the amorphous alloy by changing the overheating treatment temperature of the amorphous alloy melt, thereby achieving the purpose of regulating and controlling the performance of the amorphous alloy.
In order to achieve the purpose, the invention adopts the following technical scheme:
since the macroscopic performance has high dependence and sensitivity on the density of the amorphous solid alloy, the regulation and control of the density of the amorphous alloy is one of the important ways for improving the performance of the amorphous solid alloy, but an effective process technical method is still lacked for the regulation and control of the density of the amorphous alloy at present, and the method becomes one of the key and important scientific and technical problems which cannot be solved in the field of amorphous alloys. The main reason why the density of the amorphous alloy cannot be effectively regulated is the lack of a method for regulating the density of the alloy melt. Due to the lack of technical methods for controlling the melt density, the desired melt density cannot be solidified into an amorphous solid alloy. The establishment of the technological method for regulating the density of the amorphous solid alloy is not only a critical technology for meeting the important research and engineering production of the amorphous alloy ribbon material, but also an important technology urgently needed for developing high-performance amorphous alloy ribbon materials.
Because the atom cluster structure in the melt cannot be measured through an experimental means, the simulation of the coordination number of the alloy melt by using a computer is undoubtedly an effective means for directly researching the atom cluster structure of the melt from an atom distribution level, and the atom cluster structure information of the melt can be relatively comprehensively reflected, although the information is statistical. In amorphous alloy melts, such as ferrosilicon boron alloy melts, the nonmetallic element is a key factor for the melt to form the amorphous solid alloy, because the melt can be rapidly solidified into the amorphous solid alloy only when the metallic element forms atom clusters around the nonmetallic element, so that the iron-silicon atom clusters, the iron-boron and the iron-silicon-boron atom clusters formed by centering on the nonmetallic element are the main atoms forming the amorphous solid alloyAnd (4) clustering. Bonding between atoms of the same type and between atoms of different types in the melt can be determined by the binary probability distribution function g (r) ═ ρ (r)/ρ of the alloy0Obtained in the formula rho0Is the average atomic density of the material, and ρ (r) represents the statistical average of the probability of distribution of atoms on a sphere at a distance r, centered on any atom, and reflects the state of distribution of atoms at different positions from any atom in the material. From g (r), the neighbor relation information of the atoms of the same type and different types can be obtained, although the neighbor relation information cannot give the specific spatial position of the atom distribution, the statistical average value of the number and the distance of the neighbor atoms can be given, and the method is equivalent to compressing the three-dimensional information of the atom distribution into one dimension. G (r) of the melt will peak at certain locations, indicating that other atomic numbers around a certain atom are distributed at distances corresponding to the peak locations, wherein the peak closest to the origin is the location of the first adjacent atomic distribution, and the other peaks are sequentially the locations of the second, third, fourth, etc. adjacent atomic distributions as the distances increase. From this, it is understood that the number of adjacent peaks directly corresponds to the size of the atomic cluster, and that the larger the number of adjacent peaks, the larger the size of the atomic cluster becomes, and the intensity of the adjacent peaks corresponds to the number of distributions of the adjacent atoms. For the heterogeneous atoms, the closer the distance to the central atom, the stronger the interatomic interaction force, the larger the number of atoms in the distribution, and the larger the corresponding peak intensity in g (r). With the increasing distance from the central atom, the interaction force between the heterogeneous atoms is obviously weakened, the probability of forming a cluster structure by the outer layer atoms and the central atom is rapidly reduced, so that the adjacent peaks far away from the origin in g (r) disappear, and only a limited number of adjacent peaks exist in g (r) of the melt. The intensity of the peak in g (r) changes correspondingly with the change of the melt temperature, which shows the change of the structure and the size of the melt atom cluster with the change of the temperature, wherein the change of the peak intensity corresponds to the change of the number of adjacent atoms, and the change of the number of adjacent peaks corresponds to the increase and the decrease of the number of adjacent atoms. When the number of adjacent peaks is increased or decreased, the size of the atomic cluster in the melt is increased or decreased, so that the change of the size of the atomic cluster in the melt can be clearly judged from the change of the number of adjacent peaks in g (r)The situation is.
In a neighboring atomic layer, the number of atoms corresponds to the density of the atomic distribution, and therefore the larger the number of neighboring atoms, the higher the density of the atomic distribution. Since the density of the melt is proportional to the atom distribution density, the melt density is proportional to the number of neighboring atoms. Similarly, the larger the number of adjacent atomic layers, the higher the atomic distribution density in the atomic cluster, and thus the melt density is proportional to the number of adjacent atomic layers. From this, it is understood that the larger the number of adjacent atomic layers and the number of adjacent atoms per layer, the higher the melt density. The number of adjacent atoms of each layer and the number of adjacent atom layers of the melt change at different overheating temperatures, so that the density of the melt changes along with the overheating temperature. Typically, the first adjacent peak of the melt is much stronger than the other, secondary adjacent peaks, and thus, the number of atoms contained in the first adjacent peak may be considered the average atomic coordination number of the melt. The amorphous solid alloy retains the structural characteristics of the melt, and amorphous alloys with different densities can be obtained by supercooling and solidifying alloy melts with different average atomic coordination numbers into amorphous solids.
A method for regulating and controlling the density of amorphous alloy comprises the following steps:
calculating the average atomic coordination number of the amorphous alloy melt: calculating the average atomic coordination number of the amorphous alloy melt at different temperatures to obtain a calculation result of the average atomic coordination number along with the temperature change;
carrying out overheating treatment on the alloy melt: and selecting a required average atomic coordination number according to the calculation result, determining the temperature corresponding to the selected average atomic coordination number as the overheating treatment temperature of the alloy melt, and preserving the heat of the alloy melt at the overheating treatment temperature to obtain the alloy melt after overheating treatment.
A rapid solidification step: and rapidly solidifying the amorphous alloy melt after the overheating treatment to obtain the amorphous solid alloy.
In the step of calculating the average atomic coordination number of the amorphous alloy melt by simulation, as a preferred embodiment, the specific step of calculating the average atomic coordination number of the amorphous alloy melt at different temperatures is: determining an effective range of a first adjacent atomic distance according to binary distribution functions of the amorphous alloy melt at different temperatures and atomic radii (the atomic radii are all atomic radii in the amorphous alloy), and then integrating a first adjacent peak in the binary distribution functions to obtain the average atomic coordination number; preferably, the binary distribution function is calculated by a molecular dynamics simulation method; preferably, the temperature interval for calculating the average atomic coordination number of the alloy melt is 1400-1600 ℃; preferably, the effective range of the first neighboring atomic distance is 0.2-0.3 nanometers.
In the step of subjecting the alloy melt to the overheating treatment, as a preferred embodiment, after the overheating treatment temperature of the alloy melt is determined and before the alloy melt is subjected to the heat preservation, the alloy melt is heated up to the overheating treatment temperature at a rate of 5 to 15 ℃/min; preferably, the holding time is 1.5 to 3 hours, so as to bring the average atomic coordination number of the alloy melt to the same steady state as the calculated result. Since the calculation can only be carried out in an equilibrium state inside the melt, the results obtained are of course those of the equilibrium state. Therefore, if the temperature rise rate is too high, the inside of the melt is not easy to reach a uniform equilibrium state; too slow a temperature rise rate will waste unnecessary process time. Similarly, when the temperature of the melt changes to a new temperature, the melt does not reach equilibrium immediately, and must be held at this temperature for a certain period of time, if the holding time is too short, the cluster structure of the previously experienced temperature remains in the melt. If the holding time is too long, unnecessary process time will be wasted.
In the above rapid solidification step, as a preferred embodiment, the rapid solidification is performed by using a high-speed flat flow continuous casting technique; preferably, the high-speed plane flow continuous casting technology is as follows: the amorphous alloy melt is poured onto a cooling roller rotating at high speed through a nozzle to carry out rapid solidification; more preferably, the linear velocity of the chill roll surface is from 15 to 25 m/s; preferably, the amorphous solid alloy is in the form of a thin ribbon; preferably, the amorphous solid alloy has a thickness of 25-30 microns; preferably, the amorphous solid isThe width of the gold is 50-282 mm; preferably, the amorphous solid alloy is an amorphous alloy strip precursor of Fe-based, FeNi-based, FeCo-based and iron-based nanocrystalline alloys in an amorphous alloy system; more preferably, the amorphous solid alloy is Fe84Si10B6。
The invention uses the phenomenon that the average atomic coordination number of the amorphous alloy melt changes along with the overheating treatment temperature, establishes the corresponding relation between the average atomic coordination number of the amorphous alloy melt and the overheating temperature through simulation calculation, selects the proper average atomic coordination number, namely the melt density, by utilizing the overheating treatment temperature, and rapidly solidifies the melt into the amorphous solid alloy, thereby realizing the designability and controllable preparation of the amorphous alloy density.
Compared with the prior art, the invention has the following positive effects:
the invention provides a method for regulating and controlling the density of an amorphous alloy, which creates a new idea and a new method for designing and preparing an amorphous alloy microstructure.
The method is suitable for all amorphous iron-based alloy thin strips, and particularly can regulate and control the density of the amorphous iron-based alloy thin strips under the condition that the components of the alloy melt have large fluctuation.
The method has the characteristics of simple and convenient implementation, high efficiency, low cost, strong controllability and repeatability, high technical reliability and the like, and is suitable for wide application in the technical field of metal functional material preparation.
Drawings
Fig. 1 is a schematic flow chart of an amorphous alloy density control method according to the present invention.
FIG. 2 shows the present invention for Fe at 1200-1600 deg.C84Si10B6And calculating the average atomic coordination number in the alloy melt.
FIG. 3 shows the results of comparison of Fe in example 1 of the present invention84Si10B6And the schematic diagram of the measured high-resolution image of the amorphous alloy thin strip obtained after the alloy melt is subjected to overheating treatment and rapid solidification at 1600 ℃.
FIG. 4 shows the results of comparison of Fe in example 2 of the present invention84Si10B6And (3) a schematic diagram of a high-resolution image of the amorphous alloy thin strip measurement obtained after the alloy melt is subjected to overheating treatment and rapid solidification at 1300 ℃.
FIG. 5 shows the results of comparison of Fe in example 3 of the present invention84Si10B6And (3) a schematic diagram of a high-resolution image of the amorphous alloy thin strip measurement obtained after the alloy melt is subjected to overheating treatment and rapid solidification at 1400 ℃.
Detailed Description
In order that the present invention may be more readily and clearly understood, there now follows a more particular description of the invention, reference being had to the accompanying drawings.
With reference to fig. 1 to 5, the method for regulating the density of an amorphous alloy provided by the present invention comprises the following specific steps:
step 1, calculating the variation of the average atomic coordination number of the amorphous alloy melt along with the melt temperature: firstly, calculating the change of a binary distribution function of the amorphous alloy melt along with the melt temperature by using a molecular dynamics simulation method, then determining the effective range of the first adjacent atomic distance (the effective range of the first adjacent atomic distance is preferably 0.2-0.3 nm) by using the atomic radius, and respectively integrating the first adjacent peak in the binary distribution function of each temperature to obtain the average atomic coordination number. By establishing a corresponding relation between the melt temperature and the average atomic coordination number of the melt, a calculation result of the average atomic coordination number changing along with the melt temperature is obtained (as shown in FIG. 2, the average atomic coordination number decreases along with the increase of the temperature), and the calculation result is used as a basis for selecting the melt density of the alloy;
step 2, determining the overheating treatment temperature of the amorphous alloy melt according to the calculation result of the average atomic coordination number: firstly, selecting a required average atomic coordination number according to a calculation result of the average atomic coordination number of the alloy melt changing along with the melt temperature, and then determining the corresponding melt temperature according to the selected average atomic coordination number to be used as the overheating treatment temperature of the melt;
step 3, heating the amorphous alloy melt at a set temperature: setting the overheating treatment temperature of the melt, heating the alloy melt to the set overheating treatment temperature at the speed of 10 ℃/minute, and then preserving the heat for 2 hours so as to ensure that the average atomic coordination number of the melt reaches the stable state same as the calculated result;
and 4, rapidly solidifying the amorphous alloy melt after the heating treatment to obtain an amorphous alloy thin strip: continuously pouring the amorphous alloy melt after the overheating treatment onto a fast cooling copper roller rotating at a high speed through a nozzle, wherein the linear speed of the surface of the copper roller is 25 m/s, and the amorphous alloy melt after the overheating treatment is rapidly solidified into an amorphous alloy thin strip with the thickness of 25-30 microns;
step 5, measuring the density of the amorphous alloy thin strip: firstly weighing an amorphous alloy thin strip with a certain weight, putting the amorphous alloy thin strip into a container with scales and containing water, then measuring the volume of the water drained by the amorphous alloy thin strip, and dividing the volume of the drained water by the weight of the amorphous alloy thin strip to obtain the density of the amorphous alloy thin strip.
Example 1
A method for regulating and controlling the density of amorphous alloy comprises the following specific operation steps:
step 1, calculating Fe84Si10B6(subscript numbers in the formula are at%) average atomic coordination number of the alloy melt as a function of melt temperature: firstly, the molecular dynamics simulation method is utilized to calculate Fe84Si10B6The binary distribution function of the alloy melt changes with the melt temperature, then the effective range of the first adjacent atomic distance is determined to be 0.2-0.3 nm according to the atomic radius, and the first adjacent peak in the binary distribution function of each temperature is respectively integrated to obtain the average atomic coordination number. Fe is obtained by establishing the corresponding relation between the melt temperature and the average atomic coordination number of the melt84Si10B6Calculation of the mean atomic coordination number of the melt as a function of temperature, as a function of the choice of Fe84Si10B6The basis of the density of the alloy melt;
step 2, determining Fe according to the calculation result of the average atomic coordination number84Si10B6Temperature of alloy melt for heat treatment: first of all using Fe84Si10B6Calculation result of average atomic coordination number of alloy melt along with change of melt temperatureThe desired average atomic coordination number of 11 is selected, and then the corresponding melt temperature of 1600 ℃ is determined from the selected average atomic coordination number of 11 as Fe84Si10B6The temperature of the melt being superheated;
step 3, at the set temperature, the Fe is treated84Si10B6Heating the alloy melt: setting Fe according to the calculation result84Si10B6The temperature of the melt is controlled by first overheating Fe84Si10B6The alloy melt is heated to the set overheating treatment temperature of 1600 ℃ at the speed of 10 ℃/minute, and then the temperature is kept for 2 hours, so that Fe is enabled to be obtained84Si10B6The average atomic coordination number of the melt reaches the same steady state as the calculated result;
step 4, heating the treated Fe84Si10B6Rapidly solidifying the alloy melt to obtain amorphous Fe84Si10B6Alloy thin strip: the Fe after the overheating treatment at 1600 DEG C84Si10B6Continuously pouring the alloy melt onto a fast cooling copper roller rotating at a high speed through a nozzle, wherein the linear speed of the surface of the copper roller is 25 m/s, and the alloy melt is rapidly solidified into an amorphous alloy thin strip with the thickness of 30 microns;
step 5, measuring the density of the amorphous alloy thin strip: firstly weighing an amorphous alloy thin strip with the weight of 5 kilograms, putting the amorphous alloy thin strip into a container with scales and containing water, measuring to obtain the volume of the water discharged by the amorphous alloy thin strip to be 793 cubic centimeters, and dividing the volume of the water discharged by the weight of the amorphous alloy thin strip by the volume of the water discharged to obtain the density of the amorphous alloy thin strip to be 6.3 grams/cubic centimeter.
For the amorphous solid alloy Fe obtained in the above steps84Si10B6The microstructure of the thin band was characterized and the resulting high resolution image (two-dimensional projection of the three-dimensional structure) is shown in fig. 3, where the amorphous structure is shown to be very distinct and no crystalline structure is present.
Example 2
A method for regulating and controlling the density of amorphous alloy comprises the following specific operation steps:
step 1, calculating Fe84Si10B6(subscript numbers in the formula are at%) average atomic coordination number of the alloy melt as a function of melt temperature: firstly, the molecular dynamics simulation method is utilized to calculate Fe84Si10B6The binary distribution function of the alloy melt changes with the melt temperature, then the effective range of the first adjacent atomic distance is determined to be 0.2-0.3 nm according to the atomic radius, and the first adjacent peak in the binary distribution function of each temperature is respectively integrated to obtain the average atomic coordination number. Fe is obtained by establishing the corresponding relation between the melt temperature and the average atomic coordination number of the melt84Si10B6Calculation of the mean atomic coordination number of the melt as a function of temperature, as a function of the choice of Fe84Si10B6The basis of the density of the alloy melt;
step 2, determining Fe according to the calculation result of the average atomic coordination number84Si10B6Temperature of alloy melt for heat treatment: first of all using Fe84Si10B6Calculation of the variation of the average atomic coordination number of the alloy melt with the melt temperature selects the required average atomic coordination number of 16, and then determines the corresponding melt temperature of 1300 ℃ from the selected average atomic coordination number of 16 as Fe84Si10B6The temperature of the melt being superheated;
step 3, at the set temperature, the Fe is treated84Si10B6Heating the alloy melt: setting Fe according to the calculation result84Si10B6The temperature of the melt is controlled by first overheating Fe84Si10B6The alloy melt was heated at a rate of 10 ℃/min to a set superheat temperature of 1300 ℃, and then held for 2 hours to allow Fe to be present84Si10B6The average atomic coordination number of the melt reaches the same steady state as the calculated result;
step 4, heating the treated Fe84Si10B6Rapidly solidifying the alloy melt to obtain amorphous Fe84Si10B6Alloy thin strip: fe after 1300 ℃ overheating treatment84Si10B6Continuously pouring the alloy melt onto a fast cooling copper roller rotating at a high speed through a nozzle, wherein the linear speed of the surface of the copper roller is 25 m/s, and the alloy melt is rapidly solidified into an amorphous alloy thin strip with the thickness of 25 microns;
step 5, measuring the density of the amorphous alloy thin strip: firstly weighing an amorphous alloy thin strip with the weight of 5 kilograms, putting the amorphous alloy thin strip into a container with scales and containing water, measuring to obtain that the volume of the water discharged by the amorphous alloy thin strip is 703 cubic centimeters, and dividing the weight of the amorphous alloy thin strip by the volume of the discharged water to obtain that the density of the amorphous alloy thin strip is 7.1 grams/cubic centimeter.
For the amorphous solid alloy Fe obtained in the above steps84Si10B6The microstructure of the thin band was characterized and the resulting high resolution image is shown in fig. 4, where the amorphous structure is very distinct and no crystalline structure is present.
Example 3
A method for regulating and controlling the density of amorphous alloy comprises the following specific operation steps:
step 1, calculating Fe84Si10B6(subscript numbers in the formula are at%) average atomic coordination number of the alloy melt as a function of melt temperature: firstly, the molecular dynamics simulation method is utilized to calculate Fe84Si10B6The binary distribution function of the alloy melt changes with the melt temperature, then the effective range of the first adjacent atomic distance is determined to be 0.2-0.3 nm according to the atomic radius, and the first adjacent peak in the binary distribution function of each temperature is respectively integrated to obtain the average atomic coordination number. Fe is obtained by establishing the corresponding relation between the melt temperature and the average atomic coordination number of the melt84Si10B6Calculation of the mean atomic coordination number of the melt as a function of temperature, as a function of the choice of Fe84Si10B6The basis of the density of the alloy melt;
step 2, determining Fe according to the calculation result of the average atomic coordination number84Si10B6Temperature of alloy melt for heat treatment: first of all using Fe84Si10B6The mean atomic coordination number of the alloy melt varying with the temperature of the meltCalculation results the desired average atomic coordination number of 15 was selected and the corresponding melt temperature of 1400 ℃ was determined from the selected average atomic coordination number of 15 as Fe84Si10B6The temperature of the melt being superheated;
step 3, at the set temperature, the Fe is treated84Si10B6Heating the alloy melt: setting Fe according to the calculation result84Si10B6The temperature of the melt is controlled by first overheating Fe84Si10B6The alloy melt is heated to the set overheating treatment temperature of 1400 ℃ at the speed of 10 ℃/minute, and then the temperature is kept for 2 hours, so that Fe is enabled to be contained84Si10B6The average atomic coordination number of the melt reaches the same steady state as the calculated result;
step 4, heating the treated Fe84Si10B6Rapidly solidifying the alloy melt to obtain amorphous Fe84Si10B6Alloy thin strip: fe after 1400 ℃ of overheating treatment84Si10B6Continuously pouring the alloy melt onto a fast cooling copper roller rotating at a high speed through a nozzle, wherein the linear speed of the surface of the copper roller is 25 m/s, and the alloy melt is rapidly solidified into an amorphous alloy thin strip with the thickness of 27 microns;
step 5, measuring the density of the amorphous alloy thin strip: firstly weighing an amorphous alloy thin strip with the weight of 5 kilograms, putting the amorphous alloy thin strip into a container with scales and containing water, measuring to obtain the volume of the water discharged by the amorphous alloy thin strip as 730 cubic centimeters, and dividing the weight of the amorphous alloy thin strip by the volume of the discharged water to obtain the density of the amorphous alloy thin strip as 6.8 grams/cubic centimeter.
For the amorphous solid alloy Fe obtained in the above steps84Si10B6The microstructure of the thin band was characterized and the resulting high resolution image is shown in fig. 5, where the amorphous structure is very distinct and no crystalline structure is present.
In summary, the process method for regulating the amorphous solid alloy microstructure by using the melt atom cluster configuration and the quantity can realize the regulation of the amorphous solid alloy microstructure, and is suitable for amorphous solid alloy material systems with different components. The invention obtains satisfactory effect through repeated test verification.
It should be understood that the above examples are only for clarity of illustration and are not intended to limit the embodiments. Other variations and modifications will be apparent to persons skilled in the art in light of the above description. And are neither required nor exhaustive of all embodiments. And obvious variations or modifications therefrom are within the scope of the invention.
Claims (12)
1. A method for regulating and controlling the density of amorphous alloy is characterized by comprising the following steps:
calculating the average atomic coordination number of the amorphous alloy melt: calculating the average atomic coordination number of the amorphous alloy melt at different temperatures to obtain a calculation result of the average atomic coordination number along with the temperature change; the specific steps for calculating the average atomic coordination number of the amorphous alloy melt at different temperatures are as follows: determining an effective range of a first adjacent atomic distance according to a binary distribution function of the amorphous alloy melt at different temperatures and the atomic radius, and then integrating a first adjacent peak in the binary distribution function to obtain the average atomic coordination number;
carrying out overheating treatment on the alloy melt: selecting a required average atomic coordination number according to the calculation result, determining the temperature corresponding to the selected average atomic coordination number as the overheating treatment temperature of the alloy melt, heating the alloy melt to the overheating treatment temperature at the speed of 5-15 ℃/min, and preserving the heat of the alloy melt at the overheating treatment temperature to obtain the alloy melt after overheating treatment; the heat preservation time is 1.5-3 hours;
a rapid solidification step: and rapidly solidifying the amorphous alloy melt after the overheating treatment to obtain the amorphous solid alloy.
2. A method for controlling the density of amorphous alloy as claimed in claim 1, wherein in the step of calculating the average atomic coordination number of the amorphous alloy melt, the effective range of the first neighboring atomic distance is 0.2-0.3 nm.
3. The method for controlling the density of the amorphous alloy according to claim 2, wherein the distribution function of the twinkle is calculated by a molecular dynamics simulation method.
4. A control method for amorphous alloy density according to claim 1, wherein the temperature range for calculating the average atomic coordination number of the alloy melt is 1400-1600 ℃.
5. A method for controlling the density of an amorphous alloy as claimed in claim 1, wherein the rapid solidification is performed by using a high-speed plane flow continuous casting technique.
6. A method for regulating and controlling the density of amorphous alloy according to claim 5, wherein the high-speed plane flow continuous casting technique is as follows: the rapid solidification is performed by pouring the amorphous alloy melt through a nozzle onto a cooling roller rotating at a high speed.
7. A method for controlling the density of an amorphous alloy as claimed in claim 6, wherein the linear velocity of the surface of the cooling roller is 15-25 m/s.
8. A method for controlling the density of amorphous alloy as claimed in claim 5, wherein the amorphous solid alloy is in the form of thin ribbon.
9. A method for controlling the density of amorphous alloy as claimed in claim 5, wherein the thickness of the amorphous solid alloy is 25-30 μm.
10. A method for controlling the density of amorphous alloy as claimed in claim 5, wherein the width of the amorphous solid alloy is 50-282 mm.
11. A method for controlling the density of amorphous alloy as claimed in claim 5, wherein the amorphous solid alloy is the amorphous alloy strip precursor of Fe-based, FeNi-based, FeCo-based and Fe-based nanocrystalline alloy in the amorphous alloy system.
12. The method as claimed in claim 11, wherein the amorphous solid alloy is Fe84Si10B6。
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910153140.5A CN109702157B (en) | 2019-02-28 | 2019-02-28 | Amorphous alloy density regulating and controlling method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910153140.5A CN109702157B (en) | 2019-02-28 | 2019-02-28 | Amorphous alloy density regulating and controlling method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN109702157A CN109702157A (en) | 2019-05-03 |
| CN109702157B true CN109702157B (en) | 2021-03-16 |
Family
ID=66266105
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201910153140.5A Active CN109702157B (en) | 2019-02-28 | 2019-02-28 | Amorphous alloy density regulating and controlling method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109702157B (en) |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100237145B1 (en) * | 1997-03-14 | 2000-01-15 | 윤문수 | Fe amorphous soft-magnetic material and manufacturing method thereof |
| JP2011144416A (en) * | 2010-01-14 | 2011-07-28 | Tohoku Univ | Highly conductive amorphous alloy, highly conductive amorphous alloy for light electric application and highly conductive amorphous alloy for power application |
| CN104865282B (en) * | 2015-04-30 | 2017-07-04 | 安泰科技股份有限公司 | A kind of method for characterizing non-crystaline amorphous metal microstructure |
| CN105624587B (en) * | 2015-12-29 | 2017-10-31 | 江苏非晶电气有限公司 | A kind of controllable solid-state amorphous alloy ribbon preparation method of micro-structural |
-
2019
- 2019-02-28 CN CN201910153140.5A patent/CN109702157B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN109702157A (en) | 2019-05-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| Yin et al. | Thermal behavior and grain growth orientation during selective laser melting of Ti-6Al-4V alloy | |
| Szeliga | Effect of processing parameters and shape of blade on the solidification of single-crystal CMSX-4 Ni-based superalloy | |
| Kang et al. | Macrosegregation mechanism of primary silicon phase in selective laser melting hypereutectic Al–High Si alloy | |
| Yang et al. | Heat transfer and macrostructure formation of Nb containing TiAl alloy directionally solidified by square cold crucible | |
| CN109702157B (en) | Amorphous alloy density regulating and controlling method | |
| CA1093271A (en) | Method and apparatus for the continuous casting of steel | |
| CN109797352B (en) | Method for regulating and controlling average atomic cluster size of amorphous alloy | |
| Körber et al. | Anisotropic Growth of the Primary Dendrite Arms in a Single‐Crystal Thin‐Walled Nickel‐Based Superalloy | |
| Jiang et al. | Functionally graded mold inserts by laser-based flexible fabrication: processing modeling, structural analysis, and performance evaluation | |
| US20150231696A1 (en) | Methods for directional solidification casting | |
| Wróbel et al. | Microstructure formation in micron-scale thin-walled Hastelloy X samples fabricated with laser powder bed fusion | |
| Dou et al. | Understanding the Initial Solidification Behavior for Al–Si Alloy in Cold Chamber High-Pressure Die Casting (CC-HPDC) Process Combining Experimental and Modeling Approach | |
| Cantor | Differential scanning calorimetry and the advanced solidification processing of metals and alloys | |
| CN111014600B (en) | Process method for reducing difference between casting temperature and solidification temperature of amorphous alloy melt | |
| Tan et al. | Numerical simulation on solidification behavior and structure of 38CrMoAl large round bloom using CAFE model | |
| Karpe et al. | Heat transfer analyses of continuous casting by free jet meltspinning device | |
| Cooper | Building components by laser-additive processing | |
| Wang et al. | Effect of induction heat on initial solidification during electromagnetic continuous casting of steel | |
| CN110976794A (en) | Process method for increasing thickness of amorphous alloy strip | |
| CN110976793A (en) | Process method for regulating and controlling casting temperature of amorphous alloy melt | |
| Wang et al. | A molecular dynamics simulation-based laser melting behavior analysis for Ti–Al binary alloy | |
| Yan et al. | A method for geometric features equivalence to assess the thermal behavior in the selective laser melting process | |
| Li et al. | Intelligent optimization strategy analysis of secondary cooling water distribution for billet | |
| Demir et al. | Thermoelastic stability analysis of solidification of pure metals on a coated planar mold of finite thickness | |
| Pi et al. | Simulation of jet-flow solid fraction during spray forming |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant | ||
| TR01 | Transfer of patent right | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20220630 Address after: 512026 building 56, Huangshaping Innovation Park, guanshaocheng phase I, Wujiang District, Shaoguan City, Guangdong Province Patentee after: Chuangming (Shaoguan) Green Energy Materials Technology Research Institute Co.,Ltd. Address before: No. 242, central garden, Chunjiang Town, Xinbei District, Changzhou City, Jiangsu Province, 213001 Patentee before: JIANGSU JICUI ANTAI CHUANGMING ADVANCED ENERGY MATERIALS RESEARCH INSTITUTE Co.,Ltd. |