A method and system for heat treatment of high temperature alloy parts

Abstract

The present invention relates to the field of niobium alloy heat treatment technology, and proposes a method and system for heat treatment of high temperature alloy parts, including: 2 , niobium pentoxide as raw materials are transferred to a ball mill for mixing and ball milling to obtain a mixed material; the mixed material is transferred to a smelting furnace for smelting and cooling to obtain a high niobium titanium aluminum alloy ingot; the high niobium titanium aluminum alloy ingot is subjected to hot forging to obtain a high niobium titanium aluminum alloy billet, and then hot rolled to obtain a high niobium titanium aluminum alloy thick plate; the high niobium titanium aluminum alloy thick plate is subjected to solid solution and quenching treatment to obtain a high temperature resistant high niobium titanium aluminum alloy thick plate; the solid solution temperature during solid solution treatment is adjusted in real time according to the quality analysis of the high temperature resistant high niobium titanium aluminum alloy thick plate; the high temperature resistant high niobium titanium aluminum alloy thick plate is subjected to cold rolling and laser welding to obtain a niobium alloy component. The present application improves the preparation quality of niobium alloy components by real-time regulation of the solid solution temperature during solid solution treatment.

Description

Technical Field

[0001] The present application relates to the technical field of heat treatment of niobium alloys, and in particular to a method and system for heat treatment of high-temperature alloy components. Background Art

[0002] With the development of science and technology, the requirements for high-temperature alloy components in various industries are constantly increasing, and the requirements for high-temperature alloy components required by aerospace are even higher. Among the many metal alloys of high-temperature alloy components, niobium alloy has a high melting point, high temperature resistance, and good low-temperature plasticity, and can be made into complex parts and thin plates. Therefore, it has gradually become one of the important materials for the preparation of high-temperature alloy components for aerospace. In the preparation process, vacuum heat treatment is usually required to adjust the mechanical properties of the material.

[0003] In the preparation process of niobium alloy, heat treatment includes solution treatment, quenching, etc. Niobium alloy adjusts the grain structure through heat treatment to enhance the performance of niobium alloy. However, in industrial production, heat treatment equipment works continuously with certain pre-set parameters. It is very likely that the preset parameters do not match the current alloy state, resulting in the heat treatment temperature being too high or too low, which in turn leads to uneven metal grain structure after heat treatment and reduced alloy performance.

[0004] Usually, in industrial production, relevant tests are performed on alloys after heat treatment, such as using metallographic microscopes, scanning electron microscopes, etc. to detect the microstructure of the alloy, or performing hardness tests and tensile tests on the alloy. The most commonly used method is to perform X-ray diffraction testing on the alloy after heat treatment, and to judge the uniformity of the metal grain structure of the current alloy by analyzing the peak standardization of the X-ray diffraction data. However, X-ray diffraction data is complex, and there are certain differences in the X-ray diffraction data of alloys produced due to different preparation environments, resulting in many peaks that are invalid for judging the quality of the alloy. If all peaks need to be calculated in detail when analyzing the peak data, a lot of resources and time will be wasted, and the accuracy of the metal grain structure uniformity detection will be low, and the temperature during the solution treatment cannot be adjusted in real time and accurately, and the quality of the heat treatment process cannot be effectively improved. Summary of the invention

[0005] The present application provides a method and system for heat treatment of high temperature alloy parts to solve the problem that the detection accuracy of metal grain structure uniformity is low and the temperature during solution treatment cannot be adjusted accurately in real time. The technical solutions adopted are as follows:

[0006] In a first aspect, an embodiment of the present application provides a method for heat treatment of a high temperature alloy component, the method comprising the following steps:

[0007] Titanium dioxide, aluminum powder, CaO, CaF2 , niobium pentoxide as a raw material is transferred to a ball mill for mixing and ball milling to obtain a mixed material; the mixed material is transferred to a medium frequency vacuum induction melting furnace for refining at a pressure of 0.05 Pa to obtain an alloy liquid, and then the alloy liquid is cast into a water-cooled crucible in the medium frequency vacuum induction melting furnace at a pressure of 0.05 Pa and a temperature of 1450° C., and then cooled under a vacuum environment for 6 hours to obtain a high niobium titanium aluminum alloy ingot;

[0008] The high niobium titanium aluminum alloy ingot is hot forged at a temperature of 1100°C to obtain a high niobium titanium aluminum alloy billet, which is then hot rolled to obtain a high niobium titanium aluminum alloy thick plate; the high niobium titanium aluminum alloy thick plate is subjected to solid solution treatment and quenching treatment to obtain a high temperature resistant high niobium titanium aluminum alloy thick plate; the solid solution temperature during the solid solution treatment is adjusted in real time according to the quality analysis of the high temperature resistant high niobium titanium aluminum alloy thick plate;

[0009] The high temperature resistant high niobium titanium aluminum alloy thick plate is cold rolled to obtain a cold rolled thin plate with a thickness of less than 2 mm; the cold rolled thin plate is transferred to a laser welding device for laser welding to obtain a niobium alloy component.

[0010] Preferably, the titanium dioxide, aluminum powder, CaO, CaF 2 The mass percentage of niobium pentoxide is: 27.3wt% titanium dioxide, 24.5wt% aluminum powder, 23.5wt% CaO, 14.2wt% CaF 2 , 5.5wt% niobium pentoxide.

[0011] Preferably, the ball milling treatment time is 30 minutes.

[0012] Preferably, the refining treatment is carried out at a temperature of 1600°C and for a time of 15 minutes.

[0013] Preferably, the temperature of the hot rolling treatment is 750°C.

[0014] Preferably, the temperature of the quenching treatment is 900°C.

[0015] Preferably, the method for real-time regulating the solution temperature during solution treatment according to the quality analysis of the high temperature resistant high niobium titanium aluminum alloy thick plate is:

[0016] Using an X-ray diffractometer to collect X-ray diffraction data of a high-temperature resistant high-niobium titanium aluminum alloy thick plate, and obtaining X-ray diffraction data of a standard high-temperature resistant high-niobium titanium aluminum alloy thick plate through a historical database, wherein the X-ray diffraction data includes diffraction intensity and diffraction angle;

[0017] The X-ray diffraction data of the high temperature resistant high niobium titanium aluminum alloy thick plate and the X-ray diffraction data of the standard high temperature resistant high niobium titanium aluminum alloy thick plate are respectively used as inputs of the curve fitting algorithm, and the outputs of the curve fitting algorithm are respectively used as the measured high niobium titanium alloy diffraction curve and the standard high niobium titanium alloy diffraction curve, wherein the horizontal axis of the high niobium titanium alloy diffraction curve is the diffraction angle and the vertical axis is the diffraction intensity;

[0018] According to the measured high niobium titanium alloy diffraction curve and the standard high niobium titanium alloy diffraction curve, the information contribution effectiveness of each peak point in the measured high niobium titanium alloy diffraction curve is obtained;

[0019] The information contribution effectiveness of all peak points in the measured high niobium titanium alloy diffraction curve is used as the input of the K-means clustering algorithm, and the output of the K-means clustering algorithm is used as the clustering result of the information contribution effectiveness, wherein the clustering result includes two clustering clusters;

[0020] Calculate the information contribution effectiveness mean of each cluster in the clustering result of information contribution effectiveness, take the cluster corresponding to the maximum value of the information contribution effectiveness mean as the effective peak data cluster, and take the cluster corresponding to the minimum value of the information contribution effectiveness mean as the invalid peak data cluster;

[0021] The quality standard of the measured effective high-niobium titanium-aluminum alloy thick plate diffraction sequence is obtained according to the effective peak data cluster and the invalid peak data cluster;

[0022] The measured quality standard of the effective high niobium titanium aluminum alloy thick plate diffraction sequence and the solution temperature during the solution treatment at the current moment are used as the input of the SMC controller, and the output of the SMC controller is used as the temperature adjustment signal of the high niobium titanium aluminum alloy thick plate during the solution treatment at the current moment. The solution temperature at the current moment is regulated by the temperature adjustment signal of the high niobium titanium aluminum alloy thick plate during the solution treatment at the current moment.

[0023] Preferably, the method for obtaining the information contribution effectiveness of each peak point in the measured high niobium titanium alloy diffraction curve according to the measured high niobium titanium alloy diffraction curve and the standard high niobium titanium alloy diffraction curve is:

[0024] For the measured diffraction curve of the high niobium titanium alloy, the mean diffraction intensity of all peak points in the diffraction curve of the high niobium titanium alloy is calculated, each peak point in the diffraction curve of the high niobium titanium alloy with a diffraction intensity greater than or equal to the mean diffraction intensity is taken as a high-intensity peak point, and the set composed of all the high-intensity peak points is taken as a high-intensity peak cluster; each peak point in the diffraction curve of the high niobium titanium alloy with a diffraction intensity less than the mean diffraction intensity is taken as a low-intensity peak point, and the set composed of all the low-intensity peak points is taken as a low-intensity peak cluster;

[0025] For any one of the measured high niobium titanium alloy diffraction curve and the standard high niobium titanium alloy diffraction curve, each peak point in the high niobium titanium alloy diffraction curve is taken as a target peak point, and a sequence consisting of the first preset parameter peak points closest to the target peak point, the first preset parameter peak points after the target peak point, and the target peak point in ascending order of diffraction angle is taken as a peak local feature subsequence of the target peak point;

[0026] For each peak point in the measured high niobium titanium alloy diffraction curve, when the peak point belongs to a high-intensity peak cluster, the absolute value of the difference between the diffraction intensity of the peak point and the mean value of the diffraction intensity is calculated, and the product of the diffraction intensity of the peak point and the absolute value is used as the peak intensity prominence coefficient of the peak point; when the peak point belongs to a low-intensity peak cluster, a negative mapping result with a natural constant as the base and the absolute value as the exponent is calculated, and the product of the diffraction intensity of the peak point and the negative mapping result is used as the peak intensity prominence coefficient of the peak point;

[0027] Calculate the difference between the diffraction intensity of the peak point and the diffraction intensity of any peak point in the peak local feature subsequence of the peak point, and take the product of the average of the cumulative sum of the differences on the peak local feature subsequence and the peak intensity prominence coefficient of the peak point as the information prominence of the peak point;

[0028] The cosine similarity between the local characteristic subsequence of the peak points in the measured high niobium titanium alloy diffraction curve and the local characteristic subsequence of the peak points in the standard high niobium titanium alloy diffraction curve is calculated, and the product of the cosine similarity and the information prominence of the peak point is taken as the information contribution effectiveness of the peak point.

[0029] Preferably, the method for obtaining the quality standard of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence according to the effective peak data cluster and the invalid peak data cluster is:

[0030] The sequence of peak points corresponding to all elements in the effective peak data cluster in ascending order of diffraction angle is used as the effective high-niobium titanium-aluminum alloy thick plate diffraction sequence for measurement;

[0031] The diffraction angle of each element in the invalid peak data cluster is used as each invalid diffraction angle, and the peak points corresponding to all invalid diffraction angles in the standard high niobium titanium aluminum alloy thick plate diffraction curve are removed to obtain the remaining peak points in the standard high niobium titanium aluminum alloy thick plate diffraction curve, and the sequence composed of the remaining peak points in the standard high niobium titanium aluminum alloy thick plate diffraction curve in ascending order of diffraction angle is used as the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence, and the length of the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence is the same as the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence;

[0032] The absolute value of the difference between the diffraction angle of each crest point in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence and the diffraction angle of each crest point in the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence is taken as the first component factor; the absolute value of the difference between the diffraction intensity of each crest point in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence and the diffraction intensity of each crest point in the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence is taken as the second component factor; the product of the first component factor and the second component factor is taken as the crest specific index of each crest point in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence;

[0033] The Euclidean distance between the first peak point and any peak point in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence is used as the numerator; the Euclidean distance between the first peak point and any peak point in the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence is used as the denominator; the absolute value of the inverse of the ratio of the numerator to the denominator and the sum of the second preset parameter is calculated, and the cumulative sum of the absolute value on the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence is calculated, and the negative mapping result with the natural constant as the base and the cumulative sum as the exponent is used as the first ratio factor; the cumulative sum of the peak specific index on the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence and the sum of the third preset parameter are used as the second ratio factor; the ratio of the first ratio factor to the second ratio factor is used as the peak characteristic approximation of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence;

[0034] Calculate the DTW distance between the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence and the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence, take the sum of the DTW distance and the third preset parameter as the third ratio factor, and take the ratio of the peak feature approximation to the third ratio factor as the quality standard of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence.

[0035] In a second aspect, an embodiment of the present application further provides a high-temperature alloy component heat treatment system, comprising a memory, a processor, and a computer program stored in the memory and running on the processor, wherein the processor implements the steps of any one of the above-mentioned methods when executing the computer program.

[0036] The beneficial effects of the present application are as follows: the present application analyzes the X-ray diffraction data of the high niobium titanium aluminum alloy thick plate after the heat treatment, and constructs the information contribution validity of each peak point according to the validity and prominence of the peak point data, and then divides the effective peak data cluster and the invalid peak data cluster. The quality standard is constructed according to the effective peak data cluster and the invalid peak data cluster, and the quality standard is used as the input of the SMC controller to adjust the solid solution temperature, so that the heat treatment system of the high niobium titanium aluminum alloy thick plate can adjust the solid solution temperature adaptively, improve the quality of the high temperature resistant high niobium titanium aluminum alloy thick plate, and then improve the quality of the high temperature alloy parts prepared by using the high temperature resistant high niobium titanium aluminum alloy thick plate, and solve the problem that there are many invalid peaks when using X-ray diffraction to detect the quality of the high niobium titanium aluminum alloy thick plate, and it takes more time to judge the quality of the current high niobium titanium aluminum alloy thick plate, which affects the accuracy of the solid solution temperature adjustment in the heat treatment temperature control system of the high temperature alloy parts. Therefore, the present application improves the preparation quality of high temperature niobium alloy parts by real-time regulation of the solid solution temperature during the solid solution treatment. BRIEF DESCRIPTION OF THE DRAWINGS

[0037] In order to more clearly illustrate the embodiments of the present application or the technical solutions in the prior art, the drawings required for use in the embodiments or the description of the prior art will be briefly introduced below. Obviously, the drawings described below are only some embodiments of the present application. For ordinary technicians in this field, other drawings can be obtained based on these drawings without paying creative labor.

[0038] Figure 1 A schematic flow chart of a method for heat treatment of a high-temperature alloy component provided in one embodiment of the present application;

[0039] Figure 2 A flowchart of a method for heat treatment of a high-temperature alloy component provided in one embodiment of the present application. DETAILED DESCRIPTION

[0040] The following will be combined with the drawings in the embodiments of the present application to clearly and completely describe the technical solutions in the embodiments of the present application. Obviously, the described embodiments are only part of the embodiments of the present application, not all of the embodiments. Based on the embodiments in the present application, all other embodiments obtained by ordinary technicians in this field without creative work are within the scope of protection of this application.

[0041] See also Figure 1 , which shows a flow chart of a method for heat treatment of a high-temperature alloy component provided by an embodiment of the present application, the method comprising the following steps:

[0042] Step S001, obtaining X-ray diffraction data of a high temperature resistant high niobium titanium aluminum alloy thick plate.

[0043] The present application prepares high niobium titanium aluminum alloy parts, i.e. niobium alloy parts, through a heat treatment process. The high niobium titanium aluminum alloy parts have high strength, good corrosion resistance, strong high temperature resistance, and can withstand long-term stress cycles without fatigue cracks. Therefore, the prepared high niobium titanium aluminum alloy parts can be widely used in manufacturing fuselages, wing beams, engine parts, etc. of aircraft or spacecraft. The process of the heat treatment process of the present application is as follows:

[0044] Material selection and mixing: This application uses 27.3wt% titanium dioxide, 24.5wt% aluminum powder, 23.5wt% CaO, 14.2wt% CaF 2 , 5.5wt% niobium pentoxide, and the selected materials are transferred to the ball mill for mixing using the material transfer module in the high-temperature alloy component preparation system, and the ball milling time is set to 30 minutes in the crushing module in the high-temperature alloy component preparation system.

[0045] Vacuum melting: After ball milling, the mixed material is transferred to the medium frequency vacuum induction melting furnace by the melting transmission system of the high temperature alloy component preparation system. The melting control module in the high temperature alloy component preparation system controls the medium frequency vacuum induction melting furnace to evacuate to 5×10 -2 Pa, slowly increase the smelting power until all the charge is melted, and then refine at 1600℃ for 15min.

[0046] Cooling: After refining is completed, the smelting control module controls the smelting furnace to vacuum to 5×10 -2 Pa, maintaining the temperature at 1450°C, pouring the alloy liquid into a water-cooled crucible for cooling, and after the casting is completed, cooling under vacuum for 6 hours to obtain a high niobium titanium aluminum alloy ingot.

[0047] Hot forging: The transmission module in the high-temperature alloy component preparation system transmits the high-niobium titanium-aluminum alloy ingot to the hot forging module. The hot forging temperature control system sets the hot forging temperature to 1100°C and hot forges the high-niobium titanium-aluminum alloy ingot into a high-niobium titanium-aluminum alloy billet.

[0048] Hot rolling: The high niobium titanium aluminum alloy billet is transferred to the hot rolling module through the transmission system. The hot rolling temperature control system adjusts the hot rolling temperature to 750°C, and the high niobium titanium aluminum alloy billet is hot rolled into a high niobium titanium aluminum alloy thick plate.

[0049] Heat treatment: The high niobium titanium aluminum alloy thick plate is subjected to solution treatment for 1.5 hours. After the solution treatment, it is quenched at 900°C.

[0050] After the quenching process is completed, the heat treatment of the high niobium titanium aluminum alloy thick plate is completed, and a high temperature resistant high niobium titanium aluminum alloy thick plate is obtained. This application uses a TD-3500 X-ray diffractometer to collect X-ray diffraction data of the high temperature resistant high niobium titanium aluminum alloy thick plate sample after the heat treatment. The X-ray diffraction angle is 10°-90°, and the scanning speed is 3° / min to obtain the X-ray diffraction data of the high temperature resistant high niobium titanium aluminum alloy thick plate. Since data loss may occur during data transmission, the collected X-ray diffraction data of the high temperature resistant high niobium titanium aluminum alloy thick plate is filled with data using the mean filling method. The mean filling method is a well-known technology, and this application will not repeat its process.

[0051] At this point, the X-ray diffraction data of the high temperature resistant high niobium titanium aluminum alloy thick plate is obtained, and the X-ray diffraction data includes the diffraction angle and the diffraction intensity.

[0052] Step S002, obtaining high-intensity peak clusters and low-intensity peak clusters according to X-ray diffraction data of high-temperature resistant high-niobium titanium aluminum alloy thick plates, and obtaining information contribution effectiveness according to the high-intensity peak clusters and the low-intensity peak clusters.

[0053] The main purpose of solution treatment of high niobium titanium aluminum alloy thick plates is to completely dissolve the solid solution (solid dissolved alloy elements) in the alloy, and then form a uniform crystal structure through rapid cooling, while quenching is to quickly cool the high niobium titanium aluminum alloy thick plates that have been solution treated to fix the solute in the alloy, prevent it from re-separating, and increase its hardness. In general, the crystal structure of high-quality high niobium titanium aluminum alloy thick plates produced normally is more uniform and has better performance.

[0054] Specifically, in order to improve the effect of heat treatment of high niobium titanium aluminum alloy thick plates, the obtained high temperature resistant high niobium titanium aluminum alloy thick plate X-ray diffraction data is used as input, and a curve fitting algorithm is used to output the measured high niobium titanium alloy diffraction curve, and all the peak points therein are obtained. The horizontal axis of the measured high niobium titanium alloy diffraction curve is the diffraction angle, and the vertical axis is the diffraction intensity. From the historical database, the X-ray diffraction data of the standard high temperature resistant high niobium titanium aluminum alloy thick plate that has been manually confirmed is obtained, and the curve fitting is performed using the same method to obtain a standard high niobium titanium alloy diffraction curve, and all the peak points therein are obtained. The curve fitting algorithm is a well-known technology, and this application will not repeat its process.

[0055] Furthermore, since there are many peaks in the X-ray diffraction data, the characteristic information of the alloys represented by them also has certain differences. If they need to be compared one by one, it will take a lot of time to compare many invalid peaks, wasting computing time and computing power. Therefore, it is necessary to remove some invalid peaks to improve the comparison efficiency. In the global diffraction data, the more prominent the peaks, the stronger the ability to represent the characteristic information of the alloys; in the local diffraction data, the relatively prominent peaks, the stronger the ability to represent the characteristic information of the alloys.

[0056] Specifically, for the measured high niobium titanium alloy diffraction curve, the mean diffraction intensity of all peak points in the high niobium titanium alloy diffraction curve is calculated and recorded as T, and the peak points with diffraction intensities greater than or equal to the mean T are recorded as high-intensity peak points, and all high-intensity peak points are classified into high-intensity peak clusters, and the high-intensity peak clusters are recorded as S up At the same time, all the peak points with diffraction intensity less than the mean value T are recorded as low-intensity peak points, and all low-intensity peak points are classified into low-intensity peak clusters, and the low-intensity peak clusters are recorded as S down .

[0057] For each peak point in the measured high niobium titanium alloy diffraction curve, take the first 4 peak points and the last 4 peak points, and combine the sequence of the peak points in ascending order of diffraction angle as the peak local feature subsequence, and record the peak local feature subsequence as V. Similarly, each peak point in the standard high niobium titanium alloy diffraction curve is processed in the same way to obtain the peak local feature subsequence corresponding to each peak point. It should be noted that when a peak point cannot obtain enough data to construct a peak local feature subsequence, the acquired data can be used for mean filling.

[0058] Furthermore, for the measured diffraction curve of high niobium titanium alloy, the information contribution effectiveness of each peak point is calculated:

[0059]

[0060]

[0061]

[0062] In the formula, H i is the peak intensity prominence coefficient of the i-th peak point, α i is the diffraction intensity of the ith peak point, T is the mean diffraction intensity in the measured diffraction data of the high niobium titanium aluminum alloy thick plate, e is a natural constant, i is the ith peak point, S up is a high-intensity peak cluster, S down It is a low-intensity peak cluster. iis the information prominence of the i-th peak point, R is the total number of peak points in the peak local feature subsequence of the i-th peak point, is the diffraction intensity of the jth peak point in the peak local feature subsequence of the i-th peak point. i is the information contribution effectiveness of the i-th peak point, are the local characteristic subsequences of the peaks of the i-th peak point in the measured and standard high niobium titanium alloy diffraction curves, respectively, cd() is the cosine similarity function, The cosine similarity between the i-th peak local feature subsequences in the standard high niobium titanium alloy diffraction curve is measured. The cosine similarity is a well-known technology, and the present application will not repeat the process.

[0063] When the i-th peak point belongs to a high-intensity peak, its diffraction intensity is greater than the average diffraction intensity of the measured high-niobium-titanium-aluminum alloy thick plate diffraction data, α i ×|α i The larger the value of -T|, the higher and more prominent the peak intensity is. When the i-th peak is a low-intensity peak, its peak intensity value is closer to the intensity mean of the measured high-niobium titanium aluminum alloy thick plate diffraction data. This means that the peak is more prominent among the peaks with lower intensities. When the intensity of the i-th peak in the local feature subsequence of the i-th peak is greater than that of most of the other peaks in the subsequence, The larger the value of i The larger the P i The larger the value of is, the more prominent the i-th peak point is both globally and locally, and the more prominent the information it contains is. The more similar the local feature subsequence of the measured i-th peak point is to the local feature subsequence of the standard i-th peak point, the closer the peak is to the standard peak feature, and the more likely it is to contain important information. i The larger the value of E i The larger the value is, the more effective the information contribution of the i-th peak point is, and the more relevant data of the peak should be used for judgment.

[0064] So far, the information contribution effectiveness of each peak point in the measured diffraction curve of high niobium titanium alloy is obtained.

[0065] Step S003, obtaining the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence and the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence according to the information contribution effectiveness, obtaining the quality standard degree according to the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence and the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence, and using the quality standard degree to obtain the solution temperature control result during solution treatment.

[0066] Furthermore, for the measured diffraction curve of high niobium titanium alloy, the information contribution effectiveness of all peak points is taken as input, and clustering is performed using the K-means clustering algorithm. The absolute value of the difference between the information contribution effectiveness of two peak points is used as the metric distance in the clustering process. The number of clusters is preset to 2, and the output is two clusters. K-means is a well-known technology, and the process is not described in detail in this application. The mean value of the information contribution effectiveness in each cluster is calculated, and the cluster corresponding to the largest mean value of the information contribution effectiveness is taken as the valid peak data cluster, and the cluster corresponding to the smallest mean value of the information contribution effectiveness is taken as the invalid peak data cluster. The sequence composed of the peak points corresponding to the information contribution effectiveness of all the valid peak data clusters in the ascending order of the diffraction angle is taken as the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence, and recorded as K c , and the diffraction angle and diffraction intensity of the i-th peak point are recorded as

[0067] In addition, for the peak data points in the standard high niobium titanium aluminum alloy thick plate diffraction curve, according to the diffraction angle of the peak point corresponding to the effective degree of all information contribution in the invalid peak data cluster, find the data points at the corresponding diffraction angle in the standard high niobium titanium aluminum alloy thick plate diffraction curve, and remove them from the standard high niobium titanium aluminum alloy thick plate diffraction curve, and take the sequence composed of the remaining peak points after removal in the ascending order of diffraction angle as the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence, recorded as K b , and the diffraction angle and diffraction intensity of the i-th peak point are recorded as So far, the effective high niobium titanium aluminum alloy thick plate diffraction sequence K is obtained. c and the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence K b Since both sequences are constructed by eliminating the same diffraction angle, theoretically the lengths of the two sequences are the same. When the lengths are different, the lengths of the two sequences are made the same by mean filling. Mean filling is a well-known technology and the present application will not describe the process in detail.

[0068] Furthermore, the quality standard of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence is calculated:

[0069]

[0070]

[0071]

[0072] In the formula, B i is the peak specific index of the i-th peak point in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence, are the diffraction angles of the i-th peak point in the measured and standard effective high niobium titanium aluminum alloy thick plate diffraction sequence, are the diffraction intensities of the i-th peak point in the measured and standard effective high niobium titanium aluminum alloy thick plate diffraction sequence, respectively. D is the peak characteristic approximation of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence, Z is the total number of peak points in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence, is the first peak point and the jth peak point in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence, are the first and jth peak points in the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence, respectively. dist() is the Euclidean distance function. is the Euclidean distance between the first peak point and the jth peak point in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence, is the Euclidean distance between the first peak point and the jth peak point in the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence. exp() is an exponential function with a natural constant as the base, To prevent the adjustment parameter from having a denominator of 0, F is the quality standard of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence, K c , K b are respectively the measured and standard effective high niobium titanium aluminum alloy thick plate diffraction sequences, dtw() is the dtw distance function, dtw(K c ,K b ) is the measured, standard DTW distance between the effective high niobium titanium aluminum alloy thick plate diffraction sequences. The DTW distance is a well-known technology, and the present application will not repeat the process.

[0073] When the difference between the diffraction angle and diffraction intensity of the i-th peak point in the measured effective high-niobium titanium-aluminum alloy thick plate diffraction sequence and the diffraction angle and diffraction intensity of the i-th peak point in the standard effective high-niobium titanium-aluminum alloy thick plate diffraction sequence is smaller, the first component factor The smaller the second component factor The smaller, that is The smaller it is, the lower the alienation degree of the peak is, and the closer it is to the standard peak of the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence; when the measured peak interval is more similar to the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence, The smaller the value of The larger the value, the smaller the characteristic difference between each peak point measured and the standard, that is, the second ratio factor The smaller the value of D is, the larger the final value of D is, indicating that the peak characteristics in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence are more similar to the peak characteristics in the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence, and the quality of the high temperature resistant high niobium titanium aluminum alloy thick plate after heat treatment is closer to the quality of the standard high temperature resistant high niobium titanium aluminum alloy thick plate; when the peak characteristics of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence are more similar, and the dtw distance between the measured and standard effective high niobium titanium aluminum alloy thick plate diffraction sequences is smaller, dtw(K c ,K b ) is smaller, that is, the third ratio factor The smaller it is, the larger the final F value is, which means that the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence is more similar to the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence, and the higher the quality standard of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence.

[0074] The quality standard of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence and the solution temperature during the solution treatment at the current moment are used as the input of the SMC controller, wherein the quality standard of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence is used as the system parameter in the input of the SMC controller, and the SMC controller outputs the temperature adjustment signal of the high niobium titanium aluminum alloy thick plate during the solution treatment at the current moment, and the temperature adjustment signal is the temperature value to which the solution temperature at the current moment needs to be adjusted, that is, the temperature adjustment signal is the temperature value. The high niobium titanium aluminum alloy thick plate heat treatment system regulates the solution temperature at the current moment according to the temperature adjustment signal of the high niobium titanium aluminum alloy thick plate during the solution treatment at the current moment. If the solution temperature at the current moment is lower than the temperature value of the temperature adjustment signal, the solution temperature at the current moment is increased to the temperature value of the temperature adjustment signal; if the solution temperature at the current moment is higher than the temperature value of the temperature adjustment signal, the solution temperature at the current moment is decreased to the temperature value of the temperature adjustment signal, ensuring that the solution treatment temperature has a high degree of adaptability to the state of the high niobium titanium aluminum alloy thick plate, thereby improving the quality of the high temperature resistant high niobium titanium aluminum alloy thick plate after heat treatment. The SMC controller is a well-known technology, and this application will not describe its process in detail.

[0075] At this point, the regulation of the solution temperature during the solution treatment at the current moment is completed.

[0076] Step S004, based on the adjusted solution temperature at the current moment of solution treatment, the high temperature resistant high niobium titanium aluminum alloy thick plate after heat treatment is obtained, and the high temperature resistant high niobium titanium aluminum alloy thick plate after heat treatment is subjected to cold rolling process and laser welding process to prepare high temperature alloy parts.

[0077] The heat treatment process is used to obtain a high-temperature resistant high-niobium titanium aluminum alloy thick plate with uniform grains based on the adjusted solution temperature during the current solution treatment, and the high-temperature alloy parts are prepared through the following steps. The implementation flow chart of this application is as follows Figure 2 shown.

[0078] Cold rolling: The alloy thick plate transmission system is used to transport the high-temperature resistant high-niobium-titanium-aluminum alloy thick plates with uniform grains after heat treatment to the cold rolling device. The cold rolling control system starts to execute cold rolling. After multiple cold rolling processes, cold-rolled thin plates with a thickness of less than 2 mm are obtained.

[0079] Laser welding: The design blueprint of the actual alloy parts required is transmitted to the laser welding system, and the alloy thick plate transmission system is used to transport the cold-rolled thin plates to the laser welding device. The laser welding control system controls the electron beam laser to weld the cold-rolled thin plates, and the cold-rolled thin plates are welded into the required high-temperature alloy parts, which are high-niobium titanium-aluminum alloy parts. High-niobium titanium-aluminum alloy parts play an extremely important role in the aerospace field. The excellent performance of high-niobium titanium-aluminum alloy parts enables aircraft and spacecraft to operate more safely and efficiently.

[0080] So far, a heat treatment method for high temperature alloy parts is completed.

[0081] Based on the same inventive concept as the above method, an embodiment of the present application also provides a high-temperature alloy component heat treatment system, including a memory, a processor, and a computer program stored in the memory and running on the processor, and when the processor executes the computer program, the steps of any one of the above-mentioned high-temperature alloy component heat treatment methods are implemented.

[0082] Each embodiment in this specification is described in a progressive manner, and the same or similar parts between the embodiments can be referred to each other, and each embodiment focuses on the differences from other embodiments. The above description is only a preferred embodiment of the present application and is not intended to limit the present application. Any modification, equivalent replacement, improvement, etc. made within the principles of the present application shall be included in the protection scope of the present application.

Claims

1. A method for heat treatment of high temperature alloy parts, characterized in that: The method comprises the following steps: Titanium dioxide, aluminum powder, CaO, CaF2, and niobium pentoxide are transferred as raw materials into a ball mill for mixing and ball milling to obtain a mixed material; the mixed material is transferred into a medium frequency vacuum induction melting furnace for refining at a pressure of 0.05 Pa to obtain a molten alloy, and then the molten alloy is cast into a water-cooled crucible at a pressure of 0.05 Pa and a temperature of 1450° C. in the medium frequency vacuum induction melting furnace, and then cooled under a vacuum environment for 6 hours to obtain a high niobium titanium aluminum alloy ingot; The high niobium titanium aluminum alloy ingot is hot forged at a temperature of 1100°C to obtain a high niobium titanium aluminum alloy billet, which is then hot rolled to obtain a high niobium titanium aluminum alloy thick plate; the high niobium titanium aluminum alloy thick plate is subjected to solid solution treatment and quenching treatment to obtain a high temperature resistant high niobium titanium aluminum alloy thick plate; the solid solution temperature during the solid solution treatment is adjusted in real time according to the quality analysis of the high temperature resistant high niobium titanium aluminum alloy thick plate; The high temperature resistant high niobium titanium aluminum alloy thick plate is cold rolled to obtain a cold rolled thin plate with a thickness of less than 2 mm; the cold rolled thin plate is transferred to a laser welding device for laser welding to obtain a niobium alloy component; The method for real-time regulating the solution temperature during solution treatment according to the quality analysis of the high temperature resistant high niobium titanium aluminum alloy thick plate is: Using an X-ray diffractometer to collect X-ray diffraction data of a high-temperature resistant high-niobium titanium aluminum alloy thick plate, and obtaining X-ray diffraction data of a standard high-temperature resistant high-niobium titanium aluminum alloy thick plate through a historical database, wherein the X-ray diffraction data includes diffraction intensity and diffraction angle; The X-ray diffraction data of the high temperature resistant high niobium titanium aluminum alloy thick plate and the X-ray diffraction data of the standard high temperature resistant high niobium titanium aluminum alloy thick plate are respectively used as inputs of the curve fitting algorithm, and the outputs of the curve fitting algorithm are respectively used as the measured high niobium titanium alloy diffraction curve and the standard high niobium titanium alloy diffraction curve, wherein the horizontal axis of the high niobium titanium alloy diffraction curve is the diffraction angle and the vertical axis is the diffraction intensity; According to the measured high niobium titanium alloy diffraction curve and the standard high niobium titanium alloy diffraction curve, the information contribution effectiveness of each peak point in the measured high niobium titanium alloy diffraction curve is obtained; The information contribution effectiveness of all peak points in the measured high niobium titanium alloy diffraction curve is used as the input of the K-means clustering algorithm, and the output of the K-means clustering algorithm is used as the clustering result of the information contribution effectiveness, wherein the clustering result includes two clustering clusters; Calculate the information contribution effectiveness mean of each cluster in the clustering result of information contribution effectiveness, take the cluster corresponding to the maximum value of the information contribution effectiveness mean as the effective peak data cluster, and take the cluster corresponding to the minimum value of the information contribution effectiveness mean as the invalid peak data cluster; The quality standard of the measured effective high-niobium titanium-aluminum alloy thick plate diffraction sequence is obtained according to the effective peak data cluster and the invalid peak data cluster; The quality standard of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence and the solution temperature during the solution treatment at the current moment are used as the input of the SMC controller, and the output of the SMC controller is used as the temperature adjustment signal of the high niobium titanium aluminum alloy thick plate during the solution treatment at the current moment, and the solution temperature at the current moment is regulated by the temperature adjustment signal of the high niobium titanium aluminum alloy thick plate during the solution treatment at the current moment; The method for obtaining the information contribution effectiveness of each peak point in the measured high niobium titanium alloy diffraction curve according to the measured high niobium titanium alloy diffraction curve and the standard high niobium titanium alloy diffraction curve is: For the measured diffraction curve of the high niobium titanium alloy, the mean diffraction intensity of all peak points in the diffraction curve of the high niobium titanium alloy is calculated, each peak point in the diffraction curve of the high niobium titanium alloy with a diffraction intensity greater than or equal to the mean diffraction intensity is taken as a high-intensity peak point, and the set composed of all the high-intensity peak points is taken as a high-intensity peak cluster; each peak point in the diffraction curve of the high niobium titanium alloy with a diffraction intensity less than the mean diffraction intensity is taken as a low-intensity peak point, and the set composed of all the low-intensity peak points is taken as a low-intensity peak cluster; For any one of the measured high niobium titanium alloy diffraction curve and the standard high niobium titanium alloy diffraction curve, each peak point in the high niobium titanium alloy diffraction curve is taken as a target peak point, and a sequence consisting of the first preset parameter peak points closest to the target peak point, the first preset parameter peak points after the target peak point, and the target peak point in ascending order of diffraction angle is taken as a peak local feature subsequence of the target peak point; For each peak point in the measured high niobium titanium alloy diffraction curve, when the peak point belongs to a high-intensity peak cluster, the absolute value of the difference between the diffraction intensity of the peak point and the mean value of the diffraction intensity is calculated, and the product of the diffraction intensity of the peak point and the absolute value is used as the peak intensity prominence coefficient of the peak point; when the peak point belongs to a low-intensity peak cluster, a negative mapping result with a natural constant as the base and the absolute value as the exponent is calculated, and the product of the diffraction intensity of the peak point and the negative mapping result is used as the peak intensity prominence coefficient of the peak point; Calculate the difference between the diffraction intensity of the peak point and the diffraction intensity of any peak point in the peak local feature subsequence of the peak point, and take the product of the average of the cumulative sum of the differences on the peak local feature subsequence and the peak intensity prominence coefficient of the peak point as the information prominence of the peak point; Calculate the cosine similarity between the local characteristic subsequence of the peak points in the measured high niobium titanium alloy diffraction curve and the local characteristic subsequence of the peak points in the standard high niobium titanium alloy diffraction curve, and use the product of the cosine similarity and the information prominence of the peak point as the information contribution effectiveness of the peak point; The method for obtaining the quality standard of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence according to the effective peak data cluster and the invalid peak data cluster is: The sequence of peak points corresponding to all elements in the effective peak data cluster in ascending order of diffraction angle is used as the effective high-niobium titanium-aluminum alloy thick plate diffraction sequence for measurement; The diffraction angle of each element in the invalid peak data cluster is used as each invalid diffraction angle, and the peak points corresponding to all invalid diffraction angles in the standard high niobium titanium aluminum alloy thick plate diffraction curve are removed to obtain the remaining peak points in the standard high niobium titanium aluminum alloy thick plate diffraction curve, and the sequence composed of the remaining peak points in the standard high niobium titanium aluminum alloy thick plate diffraction curve in ascending order of diffraction angle is used as the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence, and the length of the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence is the same as the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence; The absolute value of the difference between the diffraction angle of each crest point in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence and the diffraction angle of each crest point in the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence is taken as the first component factor; the absolute value of the difference between the diffraction intensity of each crest point in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence and the diffraction intensity of each crest point in the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence is taken as the second component factor; the product of the first component factor and the second component factor is taken as the crest specific index of each crest point in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence; The Euclidean distance between the first peak point and any peak point in the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence is used as the numerator; the Euclidean distance between the first peak point and any peak point in the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence is used as the denominator; the absolute value of the inverse of the ratio of the numerator to the denominator and the sum of the second preset parameter is calculated, and the cumulative sum of the absolute value on the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence is calculated, and the negative mapping result with the natural constant as the base and the cumulative sum as the exponent is used as the first ratio factor; the cumulative sum of the peak specific index on the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence and the sum of the third preset parameter are used as the second ratio factor; the ratio of the first ratio factor to the second ratio factor is used as the peak characteristic approximation of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence; Calculate the DTW distance between the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence and the standard effective high niobium titanium aluminum alloy thick plate diffraction sequence, take the sum of the DTW distance and the third preset parameter as the third ratio factor, and take the ratio of the peak feature approximation to the third ratio factor as the quality standard of the measured effective high niobium titanium aluminum alloy thick plate diffraction sequence.

2. A method for heat treatment of high temperature alloy parts according to claim 1, characterized in that: The ball milling time is 30 min.

3. A heat treatment method for high temperature alloy parts according to claim 1, characterized in that: The refining treatment was carried out at a temperature of 1600° C. and for 15 minutes.

4. A method for heat treatment of high temperature alloy parts according to claim 1, characterized in that: The temperature of the hot rolling process is 750°C.

5. A method for heat treatment of high temperature alloy parts according to claim 1, characterized in that: The temperature of the quenching treatment is 900°C.

6. A high-temperature alloy component heat treatment system, comprising a memory, a processor, and a computer program stored in the memory and running on the processor, characterized in that: When the processor executes the computer program, the steps of the method for heat treatment of a high-temperature alloy component as described in any one of claims 1 to 5 are implemented.

Images