High-temperature-resistant molybdenum-rhenium alloy with high-density dislocation and preparation process of high-temperature-resistant molybdenum-rhenium alloy

Abstract

The preparation technology comprises the steps that molybdenum dioxide powder, Re powder, Ti powder, C powder and Al powder are subjected to ball milling and mixing to obtain precursor molybdenum-rhenium composite powder, molybdenum-rhenium alloy composite powder is obtained through two-stage hydrogen reduction, then high-temperature large-deformation rotary swaging is conducted after cold isostatic pressing and pressureless sintering are conducted, and the molybdenum-rhenium alloy is obtained. And finally, the high-temperature-resistant molybdenum-rhenium alloy with high-density dislocation is obtained. The dislocation density of an alloy matrix is increased by introducing a secondary phase, the recrystallization temperature of the molybdenum-rhenium alloy is increased, ultrahigh-temperature large-deformation rotary swaging of the molybdenum-rhenium alloy is achieved, high-density dislocation is further introduced through high-temperature large-deformation rotary swaging, the high-temperature tensile strength of the molybdenum-rhenium alloy is improved, and meanwhile the plasticity and toughness of the molybdenum-rhenium alloy are improved; and a wider application prospect is provided for application of the molybdenum-rhenium alloy in a more extreme environment.

Description

Technical Field

[0001] The invention belongs to the technical field of molybdenum alloy preparation, and in particular relates to a high-temperature resistant molybdenum-rhenium alloy with high-density dislocation and a preparation process thereof. Background Art

[0002] Molybdenum-rhenium alloy has high melting point, high strength, excellent thermal stability, high temperature resistance, excellent electrical conductivity and corrosion resistance, so it is widely used in aerospace, nuclear industry, chemical industry, electronic components and other fields, such as jet engine parts, vacuum electronic device cathode, reactor and high-temperature superconducting material. In recent years, molybdenum-rhenium alloy has received more and more attention in the development of aerospace materials. How to further improve the thermal stability of molybdenum-rhenium alloy in extremely high temperature environment to meet the needs of aerospace and nuclear energy applications has become the main research hotspot of molybdenum-rhenium alloy.

[0003] Dislocation density has an important influence on the comprehensive properties of materials. According to the Hall-Petch relationship, the increase in dislocation density significantly improves the strength of the material, while a moderate dislocation density helps to improve the plasticity and toughness of the material. By adding second-phase particles, the dislocation density of the matrix can be effectively increased. These second-phase particles are dispersed in the matrix. When external stress acts, the density of dislocations around the second-phase particles will increase significantly, thereby promoting the accumulation and interaction of dislocations, which not only improves the strength of the material, but also improves the plasticity and toughness of the material to a certain extent. However, the high-temperature performance of traditional second-phase strengthened molybdenum alloys has reached a bottleneck. When the temperature exceeds 1500°C, it will lead to rapid grain growth, which has become a defect that limits the application of molybdenum alloys in higher temperature environments. Summary of the invention

[0004] To solve the above problems, the present invention provides a high-temperature resistant molybdenum-rhenium alloy with high-density dislocations and a preparation process thereof. The dislocation density of the alloy matrix is ​​increased by introducing a secondary phase, the recrystallization temperature of the molybdenum-rhenium alloy is improved, and ultra-high temperature large deformation rotary forging of the molybdenum-rhenium alloy is realized. High-density dislocations are further introduced through high-temperature large deformation rotary forging, the high-temperature tensile strength of the molybdenum-rhenium alloy is improved, and the plasticity and toughness of the molybdenum-rhenium alloy are improved, providing a broader application prospect for the application of the molybdenum-rhenium alloy in more extreme environments.

[0005] The present invention is specifically implemented by the following technical scheme. According to the preparation process of a high-temperature resistant molybdenum-rhenium alloy with high-density dislocation proposed by the present invention, the following steps are included:

[0006] (1) placing molybdenum dioxide powder, Re powder, Ti powder, C powder and Al powder in a planetary ball mill and uniformly mixing them to obtain a precursor molybdenum-rhenium composite powder;

[0007] (2) subjecting the precursor molybdenum-rhenium composite powder obtained in step (1) to two-stage hydrogen reduction to obtain a molybdenum-rhenium alloy composite powder;

[0008] (3) cold isostatic pressing and pressureless sintering are performed on the molybdenum-rhenium alloy composite powder obtained in step (2) to obtain an in-situ self-generated secondary phase strengthened molybdenum-rhenium alloy;

[0009] (4) subjecting the in-situ self-generated secondary phase strengthened molybdenum-rhenium alloy obtained in step (3) to high temperature large deformation rotary forging, during which hydrogen is introduced; high density dislocations are introduced by high temperature large deformation rotary forging to obtain a high temperature resistant molybdenum-rhenium alloy having high density dislocations.

[0010] Preferably, in step (1), the rotation speed of the planetary ball mill is 80 to 160 r / min, the mixing time is 10 to 16 h, and the ball-to-material ratio is 10:1.

[0011] Preferably, in step (1), molybdenum dioxide powder, Re powder, Ti powder, C powder and Al powder form a mixed powder, in which, in terms of weight percentage, Re powder accounts for 5% to 41% of the weight of the mixed powder, Ti powder accounts for 3.7% to 8.86% of the weight of the mixed powder, C powder accounts for 0.62% to 1.48% of the weight of the mixed powder, Al powder accounts for 0.69% to 1.66% of the weight of the mixed powder, and the rest is molybdenum dioxide powder.

[0012] Preferably, in step (2), the first stage hydrogen reduction temperature is 500-600°C, and the hydrogen flow rate is 16-20m 3 / h, keep warm for 3 to 10 hours; the second stage hydrogen reduction temperature is 950 to 1050 ° C, the hydrogen flow rate is 20 to 25m 3 / h, keep warm for 7 to 11 hours.

[0013] Preferably, in step (3), the cold isostatic pressing of the pressed blank adopts a cold isostatic press with a pressure of 200-230 MPa and a holding pressure of 15-20 min; the pressureless sintering adopts a pressureless medium frequency furnace and introduces hydrogen, the sintering temperature is 1900-2300°C, the holding time is 3-9 h, and the hydrogen flow rate is 10-15 m 3 / h.

[0014] Preferably, the blanking temperature of the high temperature large deformation rotary forging in step (4) is 1550-1700°C, and the hydrogen flow rate is 18-25m 3 / h, single deformation is 40-70%, and total deformation is >90%.

[0015] The high temperature resistant molybdenum-rhenium alloy with high dislocation density prepared by the above method has a tensile strength of 370-500 MPa at 1200°C, an elongation of 20-35%, and a dislocation density of 7×10 14 / m 2 ~8×1014 / m 2 .

[0016] The present invention also provides a high-temperature resistant molybdenum-rhenium alloy with high-density dislocation prepared according to the above method and its application as a core material for a new generation of nuclear reactors.

[0017] Compared with the prior art, the present invention has obvious advantages and beneficial effects. By means of the above technical solution, the present invention can achieve considerable technical progress and practicality, and has a wide range of utilization value, and has at least the following advantages:

[0018] The present invention ball-mills molybdenum dioxide powder, Re powder, Ti powder, C powder and Al powder to obtain a precursor molybdenum-rhenium composite powder, and then performs two-stage hydrogen reduction to obtain Ti3Al, Ti x C y (For example: TiC, TiC 0.67 etc.) and Ti x AlC y The composite powder of molybdenum-rhenium alloy reinforced by composite materials (such as Ti3AlC2, Ti2AlC, etc.) is then cold isostatically pressed and pressureless sintered, and finally subjected to high-temperature large deformation rotary forging in a hydrogen atmosphere to obtain a high-temperature resistant molybdenum-rhenium alloy with high dislocation density. Ti, Al, and C are sintered in a high-temperature reducing atmosphere for a long time to form micron-sized layered Ti3Al dispersed at the grain boundaries of the molybdenum-rhenium alloy, and a small amount of TiC is produced at the same time. During the pressureless sintering process, TiC absorbs oxygen in the grain boundaries to produce titanium dioxide. Due to long-term sintering in a high-temperature reducing atmosphere, titanium dioxide is reduced to form nano-sized spherical sub-titanium oxide dispersed inside the molybdenum-rhenium alloy grains, which increases the recrystallization temperature of the molybdenum-rhenium alloy and enables ultra-high temperature large deformation rotary forging of the molybdenum-rhenium alloy. High-density dislocations are further introduced through ultra-high temperature large deformation rotary forging, so that the dislocation density of the molybdenum-rhenium alloy is increased to 7.28×10 14 / m 2 ~7.83×10 14 / m 2 , the dislocation density of purer Mo-R alloy (2.51×10 13 / m 2 ) is improved by an order of magnitude, and the high temperature strength of the molybdenum-rhenium alloy is improved, so that the single deformation during rotary forging can be increased to 40-70%, and the total deformation is higher than 90%, and the high temperature tensile strength of the molybdenum-rhenium alloy is improved. The tensile strength at 1200°C can reach 439MPa, which is more than 90% higher than that of the molybdenum-rhenium alloy without secondary phase. At the same time, the obtained molybdenum-rhenium alloy has good plasticity and toughness. The present invention provides a broader application prospect for the application of molybdenum-rhenium alloy in more extreme environments. BRIEF DESCRIPTION OF THE DRAWINGS

[0019] Figure 1It is a SEM image of the precursor molybdenum-rhenium composite powder prepared in Examples 1 to 3 and the molybdenum-rhenium composite powder prepared in the comparative example;

[0020] Figure 2 1 is a SEM image of the in-situ self-generated secondary phase strengthened molybdenum-rhenium alloy prepared in Examples 1 to 3 and the molybdenum-rhenium alloy A prepared in the comparative example;

[0021] Figure 3 It is a SEM image of the high temperature resistant molybdenum-rhenium alloy with high density dislocation prepared in Examples 1 to 3 and the molybdenum-rhenium alloy B prepared in the comparative example;

[0022] Figure 4 It is a stress-strain curve diagram of the high temperature resistant molybdenum-rhenium alloy with high density dislocation prepared in Examples 1 to 3 and the molybdenum-rhenium alloy B prepared in the comparative example at 1200°C. DETAILED DESCRIPTION

[0023] In order to make the purpose, technical solution and advantages of the embodiments of the present invention clearer, the technical solution of the present invention will be clearly and completely described below in conjunction with specific embodiments. Obviously, the described embodiments are part of the embodiments of the present invention, not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by ordinary technicians in this field without creative work are within the scope of protection of the present invention.

[0024] The present invention is described in detail with specific examples below. If no specific conditions are specified in the following examples, they are all carried out according to conventional conditions or conditions recommended by the manufacturer. The raw materials and reagents used without specifying the manufacturer are all conventional products that can be purchased from the market.

[0025] Example 1

[0026] (1) Molybdenum dioxide powder, Re powder, Ti powder, C powder and Al powder are placed in a planetary ball mill and uniformly mixed for 10 hours. The rotation speed of the planetary ball mill is 120 r / min and the ball-to-material ratio is 10:1 to obtain a precursor molybdenum-rhenium composite powder; wherein the weight percentages of Re powder, Ti powder, C powder and Al powder in the mixed powder are 5%, 3.7%, 0.62% and 0.69% respectively, and the rest is molybdenum dioxide powder; the mixed powder refers to a mixed powder of molybdenum dioxide powder, Re powder, Ti powder, C powder and Al powder (the same below).

[0027] (2) The precursor molybdenum-rhenium composite powder obtained in step (1) is subjected to two-stage hydrogen reduction to obtain a molybdenum-rhenium alloy composite powder; the first stage hydrogen reduction temperature is 500° C., and the hydrogen flow rate is 18 m 3 / h, keep warm for 4h; the second stage hydrogen reduction temperature is 950℃, the hydrogen flow rate is 20m 3 / h, keep warm for 7h;

[0028] (3) The molybdenum-rhenium alloy composite powder obtained in step (2) was pressed in a 200 MPa cold isostatic press for 15 min, and then pressurelessly sintered in a pressureless medium frequency furnace at 1900° C. for 8 h. During the pressureless sintering, hydrogen was introduced at a hydrogen flow rate of 10 m / s. 3 / h, and obtain an in-situ self-generated secondary phase strengthened molybdenum-rhenium alloy with a density of 98.2%;

[0029] (4) subjecting the in-situ self-generated secondary phase strengthened molybdenum-rhenium alloy obtained in step (3) to high temperature large deformation rotary forging, introducing hydrogen during the rotary forging process, the blanking temperature is 1550°C, and the hydrogen flow rate is 18m 3 / h, single deformation amount is 40%, rolling is 5 times, total deformation amount is 92%, high density dislocation is introduced by high temperature large deformation rotary forging, and high temperature resistant molybdenum-rhenium alloy with high density dislocation is obtained.

[0030] According to tests, the high-temperature resistant molybdenum-rhenium alloy with high-density dislocation has a tensile strength of 372 MPa at 1200° C. and an elongation of 25%.

[0031] Example 2

[0032] (1) Molybdenum dioxide powder, Re powder, Ti powder, C powder and Al powder are placed in a planetary ball mill and uniformly mixed for 12 hours, the speed of the planetary ball mill is 100 r / min, and the ball-to-material ratio is 10:1, to obtain a precursor molybdenum-rhenium composite powder; wherein the weight percentages of Re powder, Ti powder, C powder and Al powder in the mixed powder are 14%, 7.38%, 1.23% and 1.38%, respectively, and the rest is molybdenum dioxide powder;

[0033] (2) The precursor molybdenum-rhenium composite powder obtained in step (1) is subjected to two-stage hydrogen reduction to obtain a molybdenum-rhenium alloy composite powder; the first stage hydrogen reduction temperature is 600° C., and the hydrogen flow rate is 20 m 3 / h, keep warm for 5h; the second stage hydrogen reduction temperature is 1000℃, the hydrogen flow rate is 22m 3 / h, keep warm for 8h;

[0034] (3) The molybdenum-rhenium alloy composite powder obtained in step (2) was pressed in a 220 MPa cold isostatic press for 15 min, and then pressurelessly sintered in a pressureless medium frequency furnace at 2000° C. for 6 h. During the pressureless sintering, hydrogen was introduced at a hydrogen flow rate of 15 m / s. 3 / h, to obtain an in-situ self-generated secondary phase strengthened molybdenum-rhenium alloy with a density of 98.7%;

[0035] (4) subjecting the in-situ self-generated secondary phase strengthened molybdenum-rhenium alloy obtained in step (3) to high temperature large deformation rotary forging, introducing hydrogen during the rotary forging process, the blanking temperature is 1600° C., and the hydrogen flow rate is 20 m 3 / h, single deformation of 60%, 3 rolling passes, total deformation of 95%, high-density dislocations are introduced through high-temperature large deformation rotary forging to obtain a high-temperature resistant molybdenum-rhenium alloy with high-density dislocations.

[0036] According to tests, the high-temperature resistant molybdenum-rhenium alloy with high-density dislocation has a tensile strength of 439 MPa at 1200°C and an elongation of 23.2%.

[0037] Example 3

[0038] (1) Molybdenum dioxide powder, Re powder, Ti powder, C powder and Al powder are placed in a planetary ball mill and uniformly mixed for 11 hours, the rotation speed of the planetary ball mill is 150 r / min, and the ball-to-material ratio is 10:1, to obtain a precursor molybdenum-rhenium composite powder; wherein the weight percentages of Re powder, Ti powder, C powder and Al powder in the mixed powder are 30%, 8.86%, 1.48% and 1.66% respectively, and the rest is molybdenum dioxide powder;

[0039] (2) The precursor molybdenum-rhenium composite powder obtained in step (1) is subjected to two-stage hydrogen reduction to obtain a molybdenum-rhenium alloy composite powder; the first stage hydrogen reduction temperature is 550° C., and the hydrogen flow rate is 20 m 3 / h, keep warm for 4h; the second stage hydrogen reduction temperature is 1050℃, the hydrogen flow rate is 20m 3 / h, keep warm for 7h;

[0040] (3) The molybdenum-rhenium alloy composite powder obtained in step (2) was pressed in a 230 MPa cold isostatic press for 20 min, and then pressurelessly sintered in a pressureless medium frequency furnace at 2300° C. for 4 h. During the pressureless sintering, hydrogen was introduced at a hydrogen flow rate of 15 m / s. 3 / h, to obtain an in-situ self-generated secondary phase strengthened molybdenum-rhenium alloy with a density of 99.1%;

[0041] (4) The in-situ self-generated secondary phase strengthened molybdenum-rhenium alloy obtained in step (3) is subjected to high temperature large deformation rotary forging, and hydrogen is introduced during the rotary forging process. The blanking temperature is 1700° C. and the hydrogen flow rate is 25 m 3 / h, single deformation of 70%, 2 rolling passes, total deformation of 91%, high-density dislocations were introduced by high-temperature large deformation rotary forging to obtain a high-temperature resistant molybdenum-rhenium alloy with high-density dislocations.

[0042] According to tests, the high-temperature resistant molybdenum-rhenium alloy with high-density dislocation has a tensile strength of 375 MPa at 1200°C and an elongation of 33.6%.

[0043] Comparative Example

[0044] (1) Molybdenum dioxide and Re powder were placed in a planetary ball mill and uniformly mixed for 10 hours, the rotation speed of the planetary ball mill was 120 r / min, and the ball-to-material ratio was 10:1, to obtain a molybdenum-rhenium composite powder; wherein the Re powder accounted for 28% by weight of the mixed powder, and the rest was molybdenum dioxide powder;

[0045] (2) The molybdenum-rhenium composite powder is subjected to two-stage hydrogen reduction to obtain a molybdenum-rhenium alloy powder; the first stage hydrogen reduction temperature is 600°C, and the hydrogen flow rate is 17m 3 / h, keep warm for 5h; the second stage hydrogen reduction temperature is 1000℃, the hydrogen flow rate is 20m 3 / h, keep warm for 8h;

[0046] (3) The obtained molybdenum-rhenium alloy powder was pressed in a 220 MPa cold isostatic press for 15 min, and then pressurelessly sintered in a pressureless medium frequency furnace at 2000 °C for 6 h. During the pressureless sintering, hydrogen was introduced at a hydrogen flow rate of 10 m 3 / h, to obtain molybdenum-rhenium alloy A;

[0047] (4) The molybdenum-rhenium alloy A obtained in step (3) is subjected to high-temperature large-deformation rotary forging, and hydrogen is introduced during the rotary forging process. The blanking temperature is 1550° C. and the hydrogen flow rate is 18 m 3 / h, single deformation amount is 20%, 6 rolling passes, total deformation amount is 74%, and molybdenum-rhenium alloy B is obtained.

[0048] According to the test, the tensile strength of the molybdenum-rhenium alloy at 1200°C is 195MPa and the elongation is 16.2%.

[0049] Figure 1 is a SEM image of the molybdenum-rhenium alloy composite powder prepared in step (2) of Examples 1 to 3 and the molybdenum-rhenium alloy powder prepared in step (2) of the comparative example, Figure 1 a, b, c, d correspond to Examples 1, 2, 3 and Comparative Example, respectively. It can be seen that Figure 1 The secondary phases in a, b, and c are dispersed in the molybdenum-rhenium alloy composite powder, and Figure 1 The particle size of the molybdenum-rhenium alloy composite powder shown in a, b, and c is smaller, while Figure 1 The molybdenum-rhenium alloy powder shown in (d) has a larger particle size.

[0050] Figure 2 The SEM images of the in-situ self-generated secondary phase strengthened molybdenum-rhenium alloy prepared in step (3) of Examples 1 to 3 and the molybdenum-rhenium alloy A prepared in step (3) of the comparative example are shown in FIG. Figure 2 a, b, c, d correspond to Examples 1, 2, 3 and Comparative Example, respectively. It can be seen that Figure 2 The grain sizes shown in a, b, and c are 3 to 12 μm, which is obviously larger than Figure 2 The grain size of medium d is small, and Figure 2The grain sizes of a, b, and c are more uniform, while Figure 2 The grain size of the medium d is relatively large, ranging from 25 to 50 μm, and the size is uneven, which fully demonstrates that the present invention effectively suppresses grain growth and refines the molybdenum-rhenium alloy by introducing the secondary phase.

[0051] Figure 3 The SEM images are of the high temperature resistant molybdenum-rhenium alloy with high density dislocation obtained by high temperature large deformation rotary forging in steps (4) of Examples 1 to 3 and the molybdenum-rhenium alloy B obtained in step (4) of the comparative example, Figure 3 a, b, c, d correspond to Examples 1, 2, 3 and Comparative Example, respectively. It can be seen that Figure 3 The dislocation densities of a, b, and c are 7.831×10 14 / m 2 ,7.39×10 14 / m 2 ,7.28×10 14 / m 2 , Figure 3 The dislocation density of d is 2.51×10 13 / m 2 This indicates that Examples 1 to 3 of the present invention significantly improve the dislocation density of the molybdenum-rhenium alloy by introducing the secondary phase, and increase the dislocation density of the molybdenum-rhenium alloy by one order of magnitude compared with the comparative example.

[0052] Figure 4 It is a stress-strain curve diagram of the high-temperature resistant molybdenum-rhenium alloy with high dislocation density prepared in Examples 1 to 3 and the molybdenum-rhenium alloy B prepared in the comparative example at 1200°C. It can be seen that the tensile strength of the high-temperature resistant molybdenum-rhenium alloy with high dislocation density prepared in the examples of the present application is increased by 90% to 125% compared with the comparative example, and the elongation is increased by 7 to 17.4% compared with the comparative example.

[0053] The above is only an embodiment of the present invention, and does not limit the present invention in any form. The present invention can also have other forms of embodiments according to the above structures and functions, which are not listed one by one. Therefore, any simple modification, equivalent change and modification made by any technician familiar with the profession to the above embodiment according to the technical essence of the present invention without departing from the scope of the technical solution of the present invention still falls within the scope of the technical solution of the present invention.

Claims

1. A process for preparing a high temperature resistant molybdenum-rhenium alloy with high density dislocation, characterized in that The following steps are involved: (1) placing molybdenum dioxide powder, Re powder, Ti powder, C powder and Al powder in a planetary ball mill and uniformly mixing them to obtain a precursor molybdenum-rhenium composite powder; (2) subjecting the precursor molybdenum-rhenium composite powder obtained in step (1) to two-stage hydrogen reduction to obtain a molybdenum-rhenium alloy composite powder; (3) cold isostatic pressing and pressureless sintering are performed on the molybdenum-rhenium alloy composite powder obtained in step (2) to obtain an in-situ self-generated secondary phase strengthened molybdenum-rhenium alloy; (4) subjecting the in-situ self-generated secondary phase strengthened molybdenum-rhenium alloy obtained in step (3) to high temperature large deformation rotary forging, during which hydrogen is introduced; high density dislocations are introduced by high temperature large deformation rotary forging to obtain a high temperature resistant molybdenum-rhenium alloy having high density dislocations.

2. The process for preparing the high temperature resistant molybdenum-rhenium alloy with high dislocation density as claimed in claim 1, characterized in that In step (1), the rotation speed of the planetary ball mill is 80-160 r / min, the mixing time is 10-16 h, and the ball-to-material ratio is 10:

1.

3. The preparation process of the high temperature resistant molybdenum-rhenium alloy with high dislocation density as claimed in claim 1, characterized in that In step (1), according to the weight percentage, Re powder accounts for 5% to 41% of the mixed powder weight, Ti powder accounts for 3.7% to 8.86% of the mixed powder weight, C powder accounts for 0.62% to 1.48% of the mixed powder weight, Al powder accounts for 0.69% to 1.66% of the mixed powder weight, and the rest is molybdenum dioxide powder.

4. The process for preparing the high temperature resistant molybdenum-rhenium alloy with high dislocation density as claimed in claim 1, characterized in that In step (2), the first stage hydrogen reduction temperature is 500-600°C, and the hydrogen flow rate is 16-20m 3 / h, keep warm for 3 to 10 hours; the second stage hydrogen reduction temperature is 950 to 1050 ° C, the hydrogen flow rate is 20 to 25m 3 / h, keep warm for 7 to 11 hours.

5. The process for preparing the high temperature resistant molybdenum-rhenium alloy with high dislocation density as claimed in claim 1, characterized in that In step (3), the cold isostatic pressing of the pressed blank is performed using a cold isostatic press at a pressure of 200-230 MPa for 15-20 min. The pressureless sintering is performed using a pressureless medium frequency furnace and hydrogen is introduced at a sintering temperature of 1900-2300°C for 3-9 h and a hydrogen flow rate of 10-15 m 3 / h.

6. The process for preparing the high temperature resistant molybdenum-rhenium alloy with high dislocation density as claimed in claim 1, characterized in that In step (4), the blanking temperature of high temperature large deformation rotary forging is 1550-1700°C, and the hydrogen flow rate is 18-25m 3 / h, single deformation is 40-70%, and total deformation is >90%.

7. The process for preparing the high temperature resistant molybdenum-rhenium alloy with high dislocation density as claimed in claim 1, characterized in that The high-temperature resistant molybdenum-rhenium alloy with high-density dislocation has a tensile strength of 370-500 MPa at 1200° C. and an elongation of 20-35%.

8. The process for preparing the high temperature resistant molybdenum-rhenium alloy with high dislocation density as claimed in claim 1, characterized in that The dislocation density of the high temperature resistant molybdenum-rhenium alloy with high dislocation density is 7×10 14 / m 2 ~8×10 14 / m 2 .

9. The high temperature resistant molybdenum-rhenium alloy with high density dislocation obtained by the preparation process as claimed in claim 1.

10. Use of the high temperature resistant molybdenum-rhenium alloy with high density dislocation obtained by the preparation process as claimed in claim 1 as a nuclear reactor core material.

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