CN115354227A - Ferrite martensitic steel for reactor fuel cladding material and heat treatment process thereof - Google Patents
Ferrite martensitic steel for reactor fuel cladding material and heat treatment process thereof Download PDFInfo
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- G21—NUCLEAR PHYSICS; NUCLEAR ENGINEERING
- G21C—NUCLEAR REACTORS
- G21C3/00—Reactor fuel elements and their assemblies; Selection of substances for use as reactor fuel elements
- G21C3/02—Fuel elements
- G21C3/04—Constructional details
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- G21C3/07—Casings; Jackets characterised by their material, e.g. alloys
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The invention discloses a ferrite martensite steel for a reactor fuel cladding material and a heat treatment process thereof, wherein the alloy elements comprise more than or equal to 0.12 percent and less than or equal to 0.15 percent of C, more than or equal to 9.00 percent and less than or equal to 12.00 percent of Cr, more than or equal to 1.50 percent and less than or equal to 1.80 percent of W, more than or equal to 0.18 percent and less than or equal to 0.25 percent of V, more than or equal to 0.12 percent and less than or equal to 0.18 percent of Ta, more than or equal to 0.01 percent and less than or equal to 0.015 percent of Zr, more than or equal to 0.40 percent and less than or equal to 0.50 percent of Mn, more than or equal to 1.0 percent and less than or equal to 1.5 percent of Si, more than or equal to 0.010 percent and less than or equal to 0.040 percent, and more than or equal to 0.005 percent and less than or equal to 1.5 percent of N, and the heat treatment process thereof 11 B is less than or equal to 0.01 percent, the contents of S, O and P are less than 0.005 percent, and the balance is Fe matrix. The heat treatment process comprises the following steps: and (3) carrying out high-temperature heat treatment, brine quenching and secondary tempering on the ferrite martensite steel semi-finished product to obtain the FM steel. The invention is beneficial to obtaining the ferrite martensite steel for the reactor fuel cladding material with higher mechanical strength and liquid metal corrosion resistance.
Description
Technical Field
The invention relates to the technical field of nuclear metal materials, in particular to ferrite martensitic steel for a reactor fuel cladding material and a heat treatment process thereof.
Background
Nuclear energy plays an important role in the energy structure of China at present. The method aims to solve the problem of increasing demand of human beings on energy sources in the future and further improve the safety of nuclear energy. The international forum organization of the fourth generation nuclear energy system has selected 6 concept stacks representing future development directions of nuclear energy: the research and development of the lead-cooled fast reactor are particularly concerned and paid attention to, and the research and development of the lead-cooled fast reactor are caused by the good thermal performance, the strong heat carrying capacity and the simple and reliable system equipment; low-voltage operation and large safety allowance; chemical inertia, no violent reaction with water and air, strong natural circulation capability, passive inherent safety and the like. Therefore, the lead-cooled fast reactor is expected to take the first industrial demonstration application in the IV generation nuclear energy system. However, the reliability of the fuel cladding material of the lead-cooled fast reactor is one of the main bottleneck problems restricting the future continuous development and utilization of the reactor type, and determines the feasibility, safety and economy of the nuclear energy system. Earlier studies have shown that ferrite/martensite (F/M alloy) has become the first cladding material for the advanced nuclear power system of the IV generation due to its excellent corrosion performance, radiation swelling resistance and stable thermophysical properties. To date, many studies have been conducted in various countries of the world on the design, preparation, mechanical properties and creep properties of F/M alloys, including HT9 series in the United states, FV448, EM series in France and EP450 in Russia, and the composition of the base alloy has been optimized in the range of Fe- (9-12) Cr- (1.5-3) W. Among them, fe-9Cr-2W based F/M alloy steels developed in the United states and European Union have been receiving general attention because of their excellent comprehensive properties. However, the conventional commercial F/M steel is not designed specifically for the IV-generation reactor, has considerable limitations in terms of high-temperature strength, fatigue resistance, corrosion resistance, and the like, and still performs a great deal of systematic preliminary studies in terms of material performance improvement, environmental adaptability, and the like.
Normalizing and tempering the F/M steel by the traditional heat treatment process, generally performing austenitizing normalizing treatment at 980-1050 ℃ for 30-60 min, and performing air cooling or quenching; then keeping the temperature at 750-780 ℃ for 90min, and carrying out air cooling tempering treatment. The quenching can obtain a martensite structure with high-strength dislocation density, the subsequent high-temperature tempering plays a key role in the comprehensive mechanical properties of the material, and lath fine martensite and high-density dislocation in crystal grains are organized after heat treatment; the second phase is dispersed and uniformly distributed on the prior austenite grain boundary and the subgrain boundary, and can keep good high-temperature stability; is an important internal reason for maintaining the high-temperature mechanical property of the F/M steel. However, compared with the harsh service environment of the fourth generation reactor, the conventional F/M steel for the reactor fuel cladding material cannot meet the long-term use requirement on the aspects of high-temperature mechanical property and liquid lead metal corrosion resistance.
Disclosure of Invention
The technical problem to be solved by the invention is as follows: compared with the severe service environment of a fourth-generation reactor, the conventional F/M steel for the reactor fuel cladding material cannot meet the long-term use requirement in the aspects of high-temperature mechanical property and liquid lead metal corrosion resistance.
The invention is realized by the following technical scheme:
the ferrite martensite steel for the reactor fuel cladding material comprises the following alloy elements of more than or equal to 0.12 percent and less than or equal to 0.15 percent of C, more than or equal to 9.00 percent and less than or equal to 12.00 percent of Cr, more than or equal to 1.50 percent and less than or equal to 1.80 percent of W, more than or equal to 0.18 percent and less than or equal to 0.25 percent of V, more than or equal to 0.12 percent and less than or equal to 0.18 percent of Ta, more than or equal to 0.01 percent and less than or equal to 0.015 percent of Zr, more than or equal to 0.40 percent and less than or equal to 0.50 percent of Mn, more than or equal to 1.0 percent and less than or equal to 1.5 percent of Si, more than or equal to 0.010 percent and less than or equal to 0.040 percent, more than or equal to 0.005 percent and less than or equal to 1.5 percent of N 11 B is less than or equal to 0.01 percent, the contents of S, O and P are less than 0.005 percent, and the balance is Fe matrix.
According to the invention, the contents of Si, N and B elements in the ferrite/martensite stainless steel alloy are regulated and controlled, so that the purpose of improving the content of Si is to enhance solid solution strengthening, and simultaneously, the capability of forming a compact and stable thin oxide film on the surface of the material is further improved, and the metal lead corrosion resistance of the material is further improved; the content of N is controlled and trace boron isotope 11B is added to reduce the high-temperature growth rate of a second phase in the structure, stabilize the boundaries of martensite laths, strengthen the high-temperature grain boundary strengthening and improve the high-temperature creep resistance of the material.
Further optionally, the alloying elements Si, N and 11 the contents of B are respectively as follows: si is more than or equal to 1.21 percent and less than or equal to 1.40 percent, N is more than or equal to 0.010 percent and less than or equal to 0.020 percent, and N is more than or equal to 0.006 percent and less than or equal to 0.006 percent 11 B≤0.009％。
Further alternatively, the alloying elements comprise 0.122% C,9.81% Cr,1.62% W,0.21% V,0.155% Ta,0.48% Mn,1.23% Si,0.018% N,0.011% Zr,0.008% Zr 11 The content of each element of B, O, P and S is less than 0.005 percent, and the balance is matrix Fe.
Further optionally, the total mass fraction of the remaining impurities is less than 0.01%.
A heat treatment process of a ferritic martensitic steel for a reactor fuel cladding material is used for preparing the ferritic martensitic steel for the reactor fuel cladding material, and comprises the following steps:
step 1: placing the ferrite martensite steel semi-finished product in a high-temperature environment for heat treatment, and preserving heat;
step 2: after heat preservation, taking out a sample and quenching the sample by using saline water;
and step 3: then placing the blank in a high-temperature environment for primary heat preservation and tempering;
and 4, step 4: after heat preservation, taking out the sample and quenching the sample by using saline water;
and 5: then placing the blank in a high-temperature environment for secondary heat preservation and tempering;
and 6: naturally cooling to room temperature;
in the steps, the heat treatment temperature is higher than the primary heat-preservation tempering temperature, and the primary heat-preservation tempering temperature is higher than the secondary heat-preservation tempering temperature.
Compared with the traditional one-time long-time tempering process, the novel heat treatment method can shorten the total tempering time, promote the formation of lath martensite structure and the reversion, and obtain more second phases which are finely dispersed; compared with the common heat treatment, the novel heat treatment process enables the FM steel to obtain higher high-temperature mechanical strength.
Further optionally, in the step 2 and the step 4, when the brine is quenched, the brine with the mass concentration of 10% -15% is adopted.
Further optionally, in the step 1, the ferrite martensite steel semi-finished product is placed in an environment of 1030-1060 ℃ and is subjected to heat preservation for 40-60 min.
Further optionally, in the step 3, the mixture is placed in an environment with the temperature of 710-750 ℃ and is kept for 25-40 min.
Further optionally, in the step 5, the mixture is placed in an environment with the temperature of 650-690 ℃ and is kept for 25-40 min.
Further optionally, the ferritic martensitic steel semi-finished product refers to a sample obtained by hot rolling; or the ferrite martensite steel semi-finished product is a sample prepared by smelting, homogenizing, hot forging and hot rolling raw materials of alloy element components.
The heat treatment process provided by the invention is mainly a method for carrying out rapid martensite transformation and increasing the distribution of second phase particles on a hot-rolled FM steel plate. The 10% -15% saline water quenching process in the heat treatment process aims to enable the material to be rapidly cooled and uniformly nucleated to obtain a martensite structure, and then in the continuous two-time tempering and heat preservation processes, compared with the traditional one-time long-time tempering process, the secondary heat preservation tempering process can shorten the total tempering time, promote the lath martensite structure to be formed and recover, and obtain more fine and dispersedly distributed second phases; compared with the common heat treatment, the novel heat treatment process ensures that the FM steel obtains higher high-temperature mechanical strength.
The method mainly comprises the following steps: firstly placing the mixture into a high-temperature furnace at 1030-1060 ℃, preserving heat for 45min after the furnace temperature is stable, then discharging the mixture out of the furnace, immediately quenching the mixture by using 10-15% saline water, then placing the mixture into a high-temperature furnace at 730 ℃, preserving heat for 30min after the furnace temperature is stable, rapidly cooling the mixture out of the furnace by using 10-15% saline water, then placing the mixture into a high-temperature furnace at 660 ℃, preserving heat for 30min after the furnace temperature is stable, and naturally cooling the mixture out of the furnace to room temperature.
The invention has the following advantages and beneficial effects:
the invention improves the heat treatment process of the material by regulating and controlling the component structure of the F/M steel of the cladding material so as to improve the mechanical property of the material and simultaneously increase the corrosion resistance of the material, thereby obtaining the ferrite martensite steel (FM steel for short) for the reactor fuel cladding material with higher mechanical strength and liquid metal corrosion resistance.
According to the invention, the contents of Si, N and B elements in the ferrite/martensite stainless steel alloy are regulated and controlled, so that the purpose of improving the content of Si is to enhance solid solution strengthening, and simultaneously, the capability of forming a compact and stable thin oxide film on the surface of the material is further improved, and the metal lead corrosion resistance of the material is further improved; the N content is controlled, and trace boron isotope 11B is added to reduce the high-temperature growth rate of a second phase in the structure, stabilize the boundaries of martensite laths, strengthen the high-temperature grain boundary strengthening and improve the high-temperature creep resistance of the material. Compared with the traditional one-time long-time tempering process, the novel heat treatment method has the advantages that the total tempering time can be shortened, the lath martensite structure is promoted to be formed and to be restored, and more fine and dispersed second phases are obtained; compared with the common heat treatment, the novel heat treatment process enables the FM steel to obtain higher high-temperature mechanical strength.
The tensile strength at room temperature of the ferrite martensite steel obtained by the invention is improved to 820MPa, the tensile strength at 550 ℃ is improved to 494MPa, the tensile strength at 600 ℃ is improved to 460MPa, and compared with the common heat treatment, the average mechanical strength is improved by about 50MPa. The ferrite/martensite steel alloy not only has good high-temperature mechanical property and structure thermal stability, but also has higher corrosion resistance; can better meet the high-temperature use requirement of reactor fuel cladding material FM steel.
Drawings
The accompanying drawings, which are included to provide a further understanding of the embodiments of the invention and are incorporated in and constitute a part of this application, illustrate embodiment(s) of the invention and together with the description serve to explain the principles of the invention. In the drawings:
fig. 1 is a flowchart of a heat treatment process of FM steel for reactor fuel cladding material according to an embodiment of the present invention.
FIG. 2 is a scanning electron microscope image of the corrosion layer structure of FM steel for reactor fuel cladding material after corrosion in liquid lead bismuth according to an embodiment of the invention.
FIG. 3 is a structural morphology of FM steel for reactor fuel cladding material according to an embodiment of the invention.
FIG. 4 is a SEM microstructure of FM steel for reactor fuel cladding material according to an embodiment of the invention.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the present invention is further described in detail below with reference to examples and the accompanying drawings, and the exemplary embodiments and descriptions thereof are only used for explaining the present invention and are not used as limiting the present invention.
In the following description, numerous specific details are set forth in order to provide a thorough understanding of the present invention. However, it will be apparent to those of ordinary skill in the art that: it is not necessary to employ these specific details to practice the present invention. In other instances, well-known structures, circuits, materials, or methods have not been described in detail so as not to obscure the present invention.
Throughout the specification, reference to "one embodiment," "an embodiment," "one example," or "an example" means: the particular features, structures, or characteristics described in connection with the embodiment or example are included in at least one embodiment of the invention. Thus, the appearances of the phrase "one embodiment," "an embodiment," "one example" or "an example" in various places throughout this specification are not necessarily all referring to the same embodiment or example. Furthermore, the particular features, structures, or characteristics may be combined in any suitable combination and/or sub-combination in one or more embodiments or examples. Further, those of ordinary skill in the art will appreciate that the illustrations provided herein are for illustrative purposes and are not necessarily drawn to scale. As used herein, the term "and/or" includes any and all combinations of one or more of the associated listed items.
Example 1
The embodiment provides a ferritic martensitic steel (FM steel for short) for a reactor fuel cladding material, which can meet engineering requirements and is obtained by the following preparation process:
(1) The FM steel for the cladding material comprises the following alloy elements in percentage by mass: 0.131% C,9.81% by weight of Cr,1.62% by weight of W,0.21% by weight of V,0.155% by weight of Ta,0.48% by weight of Mn,1.23% by weight of Si,0.018% by weight of N,0.011% by weight of Zr,0.009% 11 The content of each element of B, O, P and S is less than 0.005 percent, and the balance is matrix Fe.
(2) Mixing high-purity iron, iron carbide, chromium, tungsten, vanadium, tantalum, manganese, silicon, ferroboron and sponge zirconium according to a certain proportion, wherein the proportion of each element component meets the mass percentage in the step (1), carrying out vacuum induction melting and electroslag remelting to obtain a cast ingot with uniform components, carrying out homogenization treatment at 1150 ℃, carrying out heat preservation for 120min, and carrying out hot forging, wherein the forging ratio is about 20%.
(3) And (3) preserving the temperature of the forged blank obtained in the step (2) at 1080 ℃ for 2 hours, starting hot rolling, wherein the finish rolling temperature of the hot rolled blank is not lower than 850 ℃, the single-pass rolling deformation is about 20%, and the total deformation is not lower than 80%.
(4) The hot rolled steel is subjected to heat treatment, the process is shown as figure 1, and the specific heat treatment process comprises the following steps:
firstly, putting steel into a high-temperature furnace with the furnace temperature of 1030 ℃ for heating, and preserving heat for 45min after the furnace temperature is stable;
then, quickly discharging the material out of the furnace, quenching the material in 15% saline solution, and washing the salt-containing oxide skin on the surface of the material by using clear water;
then, heating the mixture in a high-temperature furnace at 730 ℃, and preserving the temperature for 30min after the furnace temperature is stable;
then, the secondary brine is discharged from the furnace and rapidly cooled, and is washed by clear water;
and finally, placing the mixture in a 660-DEG C high-temperature furnace, preserving the temperature for 30min after the furnace temperature is stable, and then discharging the mixture out of the furnace and naturally cooling the mixture to the room temperature.
Example 2
The embodiment provides a ferritic martensitic steel (FM steel for short) for a reactor fuel cladding material, which can meet engineering requirements and is obtained by the following preparation process:
(1) The FM steel for the cladding material comprises the following alloy elements in percentage by mass: 0.131% C,10.15% by weight of Cr,1.62% by weight of W,0.21% by weight of V,0.155% by weight of Ta,0.48% by weight of Mn,1.36% by weight of Si,0.011% by weight of N,0.011% by weight of Zr,0.006% by weight of Zr 11 The content of each element of B, O, P and S is less than 0.005 percent, and the balance is matrix Fe.
(2) Mixing high-purity iron, iron carbide, chromium, tungsten, vanadium, tantalum, manganese, silicon, ferroboron and sponge zirconium according to a certain proportion, wherein the proportion of each element component meets the mass percentage in the step (1), carrying out vacuum induction melting and electroslag remelting to obtain a cast ingot with uniform components, carrying out homogenization treatment at 1150 ℃, carrying out heat preservation for 120min, and carrying out hot forging, wherein the forging ratio is about 20%.
(3) And (3) preserving the temperature of the forging blank obtained in the step (2) for 2 hours at 1080 ℃, starting hot rolling, wherein the finish rolling temperature of the hot rolling blank is not lower than 850 ℃, the single-pass rolling deformation is about 20 percent, and the total deformation is not lower than 80 percent.
(4) The hot rolled steel is subjected to heat treatment, and the specific heat treatment process comprises the following steps:
firstly, placing steel into a high-temperature furnace with the furnace temperature of 1060 ℃ for heating, and preserving heat for 60min after the furnace temperature is stable;
then, quickly discharging the material out of the furnace, quenching the material in 15% saline solution, and washing the salt-containing oxide skin on the surface of the material by using clear water;
then, heating the mixture in a high-temperature furnace at 730 ℃, and keeping the temperature for 25min after the furnace temperature is stable;
then, the secondary brine is discharged from the furnace and is quickly cooled and washed by clear water;
and finally, placing the mixture in a 660-DEG C high-temperature furnace, keeping the temperature for 25min after the furnace temperature is stable, and then discharging the mixture out of the furnace and naturally cooling the mixture to the room temperature.
Example 3
The embodiment provides a ferritic martensitic steel (FM steel for short) for a reactor fuel cladding material, which can meet engineering requirements and is obtained by the following preparation process:
(1) The FM steel for the cladding material comprises the following alloy elements in percentage by mass: 0.125% C,10.11% by weight, 1.75% by weight, 0.25% by weight of the V,0.165% by weight of the Ta,0.45% by weight of the Mn,1.41% by weight of Si,0.015% by weight of N,0.011% Zr,0.008% 11 The content of each element of B, O, P and S is less than 0.005 percent, and the balance is matrix Fe.
(2) Mixing high-purity iron, iron carbide, chromium, tungsten, vanadium, tantalum, manganese, silicon, ferroboron and sponge zirconium according to a certain proportion, wherein the proportion of each element component meets the mass percentage in the step (1), carrying out vacuum induction melting and electroslag remelting to obtain a cast ingot with uniform components, carrying out homogenization treatment at 1150 ℃, carrying out heat preservation for 120min, and carrying out hot forging, wherein the forging ratio is about 20%.
(3) And (3) preserving the temperature of the forging blank obtained in the step (2) for 2 hours at 1080 ℃, starting hot rolling, wherein the finish rolling temperature of the hot rolling blank is not lower than 850 ℃, the single-pass rolling deformation is about 20 percent, and the total deformation is not lower than 80 percent.
(4) The hot rolled steel is subjected to heat treatment, and the specific heat treatment process comprises the following steps:
firstly, placing steel into a high-temperature furnace with the furnace temperature of 1060 ℃ for heating, and preserving heat for 40min after the furnace temperature is stable;
then, quickly discharging the materials out of the furnace, quenching the materials in 15% saline solution, and washing salt-containing oxide skin on the surface of the materials by using clear water;
then, heating the mixture in a high-temperature furnace at 730 ℃, and keeping the temperature for 30min after the furnace temperature is stable;
then, the secondary brine is discharged from the furnace and is quickly cooled and washed by clear water;
and finally, placing the mixture in a 660-DEG C high-temperature furnace, preserving the temperature for 30min after the furnace temperature is stable, and then discharging the mixture out of the furnace and naturally cooling the mixture to the room temperature.
Example 4
The embodiment provides a ferritic martensitic steel (FM steel for short) for a reactor fuel cladding material, which can meet engineering requirements and is obtained by the following preparation process:
(1) The FM steel for the cladding material comprises the following alloy elements in percentage by mass: 0.140% C,9.95% by weight, 1.55% by weight, 0.25% by weight of the V,0.151% by weight of the Ta,0.45% by weight of the Mn,1.36% by weight of Si,0.012% by weight of N,0.011% Zr,0.008% 11 The content of each element of B, O, P and S is less than 0.005 percent, and the balance is matrix Fe.
(2) Mixing high-purity iron, iron carbide, chromium, tungsten, vanadium, tantalum, manganese, silicon, ferroboron and sponge zirconium according to a certain proportion, wherein the proportion of each element component meets the mass percentage in the step (1), carrying out vacuum induction melting and electroslag remelting to obtain a cast ingot with uniform components, carrying out homogenization treatment at 1150 ℃, carrying out heat preservation for 120min, and carrying out hot forging, wherein the forging ratio is about 20%.
(3) And (3) preserving the temperature of the forging blank obtained in the step (2) for 2 hours at 1080 ℃, starting hot rolling, wherein the finish rolling temperature of the hot rolling blank is not lower than 850 ℃, the single-pass rolling deformation is about 20 percent, and the total deformation is not lower than 80 percent.
(4) The hot rolled steel is subjected to heat treatment, and the specific heat treatment process comprises the following steps:
firstly, putting steel into a high-temperature furnace with the furnace temperature of 1030 ℃ for heating, and preserving heat for 60min after the furnace temperature is stable;
then, quickly discharging the materials out of the furnace, quenching the materials in 15% saline solution, and washing salt-containing oxide skin on the surface of the materials by using clear water;
then, heating the mixture in a high-temperature furnace at 730 ℃, and preserving heat for 40min after the furnace temperature is stable;
then, the secondary brine is discharged from the furnace and rapidly cooled, and is washed by clear water;
and finally, placing the mixture in a 660-DEG C high-temperature furnace, keeping the temperature for 40min after the furnace temperature is stable, and then discharging the mixture out of the furnace and naturally cooling the mixture to the room temperature.
Comparative example 1
Comparative example 1 provides an FM steel alloy which differs from example 4 in that no Si, N, ti, or Ti is added, 11 And B element.
Soaking the FM steel of the embodiments 1-4 and the comparative example 1 in a liquid lead-bismuth alloy at 550 ℃ for continuous corrosion for 800h, and observing the thickness of a corrosion product by using a scanning electron microscope under the condition of not controlling the oxygen concentration; the specific corrosion method and the conventional technology for observing and testing the thickness of the corrosion layer by a scanning electron microscope are not described herein. The corrosion structure and the corrosion layer thickness were observed as shown in fig. 2, and the test results are shown in table 1 below.
Table 1 comparison of the thickness of the corrosion layer after corrosion testing of examples 1 to 4 with comparative example 1 in liquid lead bismuth alloys
| Sample examples | Thickness of outer layer etching layer/. Mu.m | Thickness of inner layer etching layer/. Mu.m | Total etch layer thickness/. Mu.m |
| Comparative example 1 | 38.2 | 12.1 | 50.3 |
| Real-time example 1 | 29.5 | 9.6 | 39.1 |
| Examples2 | 25.9 | 8.8 | 34.7 |
| Example 3 | 27.3 | 9.0 | 36.3 |
| Example 4 | 28.8 | 10.1 | 38.9 |
According to the attached figure 2, after the FM steel is corroded in the liquid lead bismuth, the corrosion layer is composed of three obvious layers, wherein corrosion products of the outer layer and the inner layer directly influence the long-term corrosion resistance of the material, and the thicker the corrosion layers of the outer layer and the inner layer are, the poorer the corrosion resistance of the material to the liquid lead bismuth is; as shown in table 1, the thicknesses of the outer corrosion layer and the inner corrosion layer of examples 1 to 4 are smaller than that of comparative example 1, so that examples 1 to 4 have better liquid lead bismuth corrosion resistance compared with comparative example 1. The FM steel for cladding material obtained in the above example 1 has a grain size of 8 μm to 14 μm, and has a subgrain structure in lath martensite, contains relatively high density of dislocations, and is dispersed with a large amount of second phases along the vicinity of grain boundaries, and the structure morphology is shown in FIG. 3, and the transmission electron microscope structure morphology is shown in FIG. 4. As can be seen from fig. 3, the FM steel provided in example 1 had martensite and a small amount of ferrite as the main microstructure; as can be seen from fig. 4, the FM steel provided in example 1 has a structure in which fine second phases are dispersed, and thus the high-temperature mechanical properties of the FM steel can be improved. It can be seen that the FM steel after the above heat treatment has a structure of lath martensite, a small amount of ferrite, and a fine dispersed second phase. The texture shape is beneficial to maintaining the high-temperature stability of the FM steel, and the design requirement is met.
Comparative example 2
Comparative example 2 provides an FM steel alloy, which is the same as example 4 in preparation steps except for a different heat treatment method, and the specific heat treatment process steps are as follows:
firstly, putting steel into a high-temperature furnace with the furnace temperature of 1030 ℃ for heating, and preserving heat for 45min after the furnace temperature is stable;
then, tapping the steel, and quickly quenching the steel by using tap water;
then, the mixture is put into a high-temperature furnace at 730 ℃ for heating, after the furnace temperature is stable, the temperature is kept for 90min, and then the mixture is taken out of the furnace and is naturally cooled to the room temperature.
The FM steels prepared in examples 1 to 4 and comparative example 2 were subjected to room temperature and high temperature mechanical tensile property measurement:
the normal temperature and high temperature mechanical properties of the FM steels of the specific examples 1 to 4 and the comparative example 2 were measured according to GB/T228.1-2010 "part 1 of the tensile test of metallic materials: room temperature test method and GBT 4338-2006 Metal Material high temperature tensile test method. The results of the measurements are given in table 2 below:
table 2 results of mechanical tensile test of examples 1 to 4 and comparative example 2
According to the table 2, the novel heat treatment process is adopted in the examples 1 to 4, and compared with the conventional heat treatment process comparative example 2, the mechanical tensile strength of the FM steel of the cladding material has obvious influence; for example 4 and comparative example 2 with the same component content, the tensile strength at room temperature is 839MPa and 775MPa respectively, and the tensile strength is improved by 64MPa; at 550 ℃, the tensile strength is 487MPa and 435MPa respectively, and the tensile strength is improved by more than 50MPa; at 600 ℃, the tensile strength is 460MPa and 412MPa respectively, and the tensile strength is increased by nearly 50MPa; therefore, compared with the conventional heat treatment, the heat treatment process provided by the invention can improve the room-temperature and high-temperature mechanical strength of the FM steel and can better meet the high-temperature use requirement of the reactor fuel cladding material FM steel.
The above-mentioned embodiments are intended to illustrate the objects, technical solutions and advantages of the present invention in further detail, and it should be understood that the above-mentioned embodiments are merely exemplary embodiments of the present invention, and are not intended to limit the scope of the present invention, and any modifications, equivalent substitutions, improvements and the like made within the spirit and principle of the present invention should be included in the scope of the present invention.
Claims (10)
1. The ferrite martensite steel for the reactor fuel cladding material is characterized in that the alloy elements comprise more than or equal to 0.12 percent and less than or equal to 0.15 percent of C, more than or equal to 9.00 percent and less than or equal to 12.00 percent of Cr, more than or equal to 1.50 percent and less than or equal to 1.80 percent of W, more than or equal to 0.18 percent and less than or equal to 0.25 percent of V, more than or equal to 0.12 percent and less than or equal to 0.18 percent of Ta, more than or equal to 0.01 percent and less than or equal to 0.015 percent of Zr, more than or equal to 0.40 percent and less than or equal to 0.50 percent of Mn, more than or equal to 1.0 percent and less than or equal to 1.5 percent of Si, more than or equal to 0.010 percent and less than or equal to 0.040 percent, more than or equal to 0.005 percent and less than or equal to 0.5 percent of N 11 B is less than or equal to 0.01 percent, the contents of S, O and P are less than 0.005 percent, and the balance is Fe matrix.
2. The ferritic martensitic steel for reactor fuel cladding material as set forth in claim 1, characterized in that the alloying elements Si, N and 11 the contents of B are respectively: si is more than or equal to 1.21 percent and less than or equal to 1.40 percent, N is more than or equal to 0.010 percent and less than or equal to 0.020 percent, and N is more than or equal to 0.006 percent and less than or equal to 0.006 percent 11 B≤0.009％。
3. The ferritic martensitic steel for reactor fuel cladding material as set forth in claim 1 or 2 wherein the alloy elements include 0.122% C,9.81% Cr,1.62% W,0.21% V,0.155% Ta,0.48% Mn,1.23% Si,0.018% N,0.011% Zr,0.008% Zr 11 The content of each element of B, O, P and S is less than 0.005 percent, and the balance is matrix Fe.
4. The ferritic martensitic steel for reactor fuel cladding material as claimed in claim 1 wherein the total mass fraction of the remaining impurities is less than 0.01%.
5. A process for the heat treatment of a ferritic martensitic steel for reactor fuel cladding material, for the preparation of a ferritic martensitic steel for reactor fuel cladding material according to any one of claims 1 to 4, comprising the steps of:
step 1: placing the ferrite martensite steel semi-finished product in a high-temperature environment for heat treatment, and preserving heat;
and 2, step: after heat preservation, taking out a sample and quenching the sample by using saline water;
and 3, step 3: then placing the blank in a high-temperature environment for primary heat preservation and tempering;
and 4, step 4: after heat preservation, taking out the sample and quenching the sample by using saline water;
and 5: then placing the blank in a high-temperature environment for secondary heat preservation and tempering;
and 6: naturally cooling to room temperature;
in the above steps, the heat treatment temperature is higher than the primary heat preservation tempering temperature, and the primary heat preservation tempering temperature is higher than the secondary heat preservation tempering temperature.
6. The heat treatment process of ferrite martensitic steel for reactor fuel cladding material as claimed in claim 5, characterized in that in step 2 and step 4, brine with a mass concentration of 10% -15% is adopted during brine quenching.
7. The heat treatment process of the ferritic martensitic steel for the reactor fuel cladding material as claimed in claim 5, characterized in that in step 1, the ferritic martensitic steel semi-finished product is placed in an environment of 1030-1060 ℃ and kept warm for 40-60 min.
8. The heat treatment process of the ferritic martensitic steel for the reactor fuel cladding material as claimed in claim 5, characterized in that in step 3, the steel is placed in an environment with a temperature of 710-750 ℃ and is kept warm for 25-40 min.
9. The heat treatment process of ferrite martensite steel for reactor fuel cladding material as claimed in claim 5, wherein in step 5, the steel is placed in an environment of 650-690 ℃ and kept warm for 25-40 min.
10. The heat treatment process of a ferritic martensitic steel for reactor fuel cladding material as claimed in claim 5 wherein the ferritic martensitic steel semi-finished product is a sample obtained by hot rolling; or the ferrite martensite steel semi-finished product is a sample prepared by smelting, homogenizing, hot forging and hot rolling the raw materials of the alloy element components.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115786817A (en) * | 2022-12-09 | 2023-03-14 | 中国核动力研究设计院 | High-strength and high-toughness stainless steel material for advanced reactor structural material and application thereof |
Citations (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1544312A1 (en) * | 2003-12-19 | 2005-06-22 | Korea Atomic Energy Research Institute | Method of producing heat-resistant high chromium ferritic/martensitic steel |
| WO2015127523A1 (en) * | 2014-02-28 | 2015-09-03 | Vallourec Tubos Do Brasil S.A. | Martensitic-ferritic stainless steel, manufactured product and processes using the same |
| CN106119730A (en) * | 2016-08-23 | 2016-11-16 | 中国科学院合肥物质科学研究院 | A kind of low activation martensitic steel with high-temperature mechanical property and heat-treatment technology method |
| CN107130185A (en) * | 2017-06-13 | 2017-09-05 | 中国科学院合肥物质科学研究院 | A kind of resistance to irradiation martensite steel of low activation of new dispersion-strengtherning and its Technology for Heating Processing |
| CN109536850A (en) * | 2019-01-10 | 2019-03-29 | 北京科技大学 | A kind of high tough low yield strength ratio thick steel plate and its production technology |
| CN111705268A (en) * | 2020-07-01 | 2020-09-25 | 东北大学 | Steel for low-yield-ratio ultrahigh-strength high-toughness pressure-resistant shell and preparation method thereof |
| CN112695255A (en) * | 2020-11-27 | 2021-04-23 | 中国核动力研究设计院 | Preparation method of ferrite martensite steel clad tube |
| CN113235014A (en) * | 2021-05-06 | 2021-08-10 | 中国科学院合肥物质科学研究院 | High-performance silicon-containing ferrite/martensite steel |
| CN113528952A (en) * | 2021-06-29 | 2021-10-22 | 中国原子能科学研究院 | High-silicon high-chromium ferrite/martensite heat-resistant steel resistant to liquid lead or lead bismuth corrosion and preparation method thereof |
| CN113528979A (en) * | 2020-04-21 | 2021-10-22 | 四川大学 | High-strength RAFM steel and novel heat treatment process thereof |
| CN114000035A (en) * | 2021-11-04 | 2022-02-01 | 南阳汉冶特钢有限公司 | Production method of atmospheric corrosion resistant high-strength extra-thick Q390GNH steel plate |
| CN114561614A (en) * | 2022-03-04 | 2022-05-31 | 西安交通大学 | Treatment method for improving corrosion resistance of steel material in lead or lead bismuth |
| CN114622138A (en) * | 2022-03-03 | 2022-06-14 | 上海大学 | A kind of11B-doped oxide dispersion strengthened alloy, preparation method and application thereof |
-
2022
- 2022-08-22 CN CN202211007591.6A patent/CN115354227A/en active Pending
Patent Citations (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1544312A1 (en) * | 2003-12-19 | 2005-06-22 | Korea Atomic Energy Research Institute | Method of producing heat-resistant high chromium ferritic/martensitic steel |
| WO2015127523A1 (en) * | 2014-02-28 | 2015-09-03 | Vallourec Tubos Do Brasil S.A. | Martensitic-ferritic stainless steel, manufactured product and processes using the same |
| US20170029912A1 (en) * | 2014-02-28 | 2017-02-02 | Vallourec Tubos Do Brasil S.A. | Martensitic-ferritic stainless steel, manufactured product and process using the s |
| CN106661683A (en) * | 2014-02-28 | 2017-05-10 | 搲陆瑞客巴西钢管股份公司 | Martensitic-ferritic stainless steel, manufactured product and processes using the same |
| CN106119730A (en) * | 2016-08-23 | 2016-11-16 | 中国科学院合肥物质科学研究院 | A kind of low activation martensitic steel with high-temperature mechanical property and heat-treatment technology method |
| CN107130185A (en) * | 2017-06-13 | 2017-09-05 | 中国科学院合肥物质科学研究院 | A kind of resistance to irradiation martensite steel of low activation of new dispersion-strengtherning and its Technology for Heating Processing |
| CN109536850A (en) * | 2019-01-10 | 2019-03-29 | 北京科技大学 | A kind of high tough low yield strength ratio thick steel plate and its production technology |
| CN113528979A (en) * | 2020-04-21 | 2021-10-22 | 四川大学 | High-strength RAFM steel and novel heat treatment process thereof |
| CN111705268A (en) * | 2020-07-01 | 2020-09-25 | 东北大学 | Steel for low-yield-ratio ultrahigh-strength high-toughness pressure-resistant shell and preparation method thereof |
| CN112695255A (en) * | 2020-11-27 | 2021-04-23 | 中国核动力研究设计院 | Preparation method of ferrite martensite steel clad tube |
| CN113235014A (en) * | 2021-05-06 | 2021-08-10 | 中国科学院合肥物质科学研究院 | High-performance silicon-containing ferrite/martensite steel |
| CN113528952A (en) * | 2021-06-29 | 2021-10-22 | 中国原子能科学研究院 | High-silicon high-chromium ferrite/martensite heat-resistant steel resistant to liquid lead or lead bismuth corrosion and preparation method thereof |
| CN114000035A (en) * | 2021-11-04 | 2022-02-01 | 南阳汉冶特钢有限公司 | Production method of atmospheric corrosion resistant high-strength extra-thick Q390GNH steel plate |
| CN114622138A (en) * | 2022-03-03 | 2022-06-14 | 上海大学 | A kind of11B-doped oxide dispersion strengthened alloy, preparation method and application thereof |
| CN114561614A (en) * | 2022-03-04 | 2022-05-31 | 西安交通大学 | Treatment method for improving corrosion resistance of steel material in lead or lead bismuth |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115786817A (en) * | 2022-12-09 | 2023-03-14 | 中国核动力研究设计院 | High-strength and high-toughness stainless steel material for advanced reactor structural material and application thereof |
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