CN115233107A - Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding and preparation method thereof - Google Patents
Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding and preparation method thereof Download PDFInfo
- Publication number
- CN115233107A CN115233107A CN202210900087.2A CN202210900087A CN115233107A CN 115233107 A CN115233107 A CN 115233107A CN 202210900087 A CN202210900087 A CN 202210900087A CN 115233107 A CN115233107 A CN 115233107A
- Authority
- CN
- China
- Prior art keywords
- stainless steel
- supercritical fluid
- austenitic stainless
- cooled reactor
- fluid gas
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 239000012530 fluid Substances 0.000 title claims abstract description 39
- 238000005253 cladding Methods 0.000 title claims abstract description 35
- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 34
- 238000002360 preparation method Methods 0.000 title abstract description 10
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 17
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 11
- 229910000831 Steel Inorganic materials 0.000 claims description 17
- 238000005242 forging Methods 0.000 claims description 17
- 239000010959 steel Substances 0.000 claims description 17
- 238000003723 Smelting Methods 0.000 claims description 14
- 238000001816 cooling Methods 0.000 claims description 14
- 239000000243 solution Substances 0.000 claims description 14
- 229910052804 chromium Inorganic materials 0.000 claims description 12
- 229910052799 carbon Inorganic materials 0.000 claims description 11
- 229910052758 niobium Inorganic materials 0.000 claims description 11
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 11
- 230000032683 aging Effects 0.000 claims description 10
- 229910052796 boron Inorganic materials 0.000 claims description 10
- 229910052750 molybdenum Inorganic materials 0.000 claims description 10
- 239000006104 solid solution Substances 0.000 claims description 10
- 238000000137 annealing Methods 0.000 claims description 9
- 229910052710 silicon Inorganic materials 0.000 claims description 9
- 238000002844 melting Methods 0.000 claims description 4
- 230000008018 melting Effects 0.000 claims description 4
- 239000002994 raw material Substances 0.000 claims description 4
- 238000002156 mixing Methods 0.000 claims description 3
- 238000004519 manufacturing process Methods 0.000 claims 4
- 238000000034 method Methods 0.000 claims 1
- 229910001220 stainless steel Inorganic materials 0.000 abstract description 29
- 239000011651 chromium Substances 0.000 abstract description 25
- 239000010935 stainless steel Substances 0.000 abstract description 25
- 239000000956 alloy Substances 0.000 abstract description 19
- 229910045601 alloy Inorganic materials 0.000 abstract description 18
- 229910001566 austenite Inorganic materials 0.000 abstract description 9
- 239000011159 matrix material Substances 0.000 abstract description 8
- 238000005260 corrosion Methods 0.000 abstract description 6
- 230000007797 corrosion Effects 0.000 abstract description 6
- 229910000423 chromium oxide Inorganic materials 0.000 abstract description 3
- WGLPBDUCMAPZCE-UHFFFAOYSA-N Trioxochromium Chemical compound O=[Cr](=O)=O WGLPBDUCMAPZCE-UHFFFAOYSA-N 0.000 abstract description 2
- 229910052751 metal Inorganic materials 0.000 abstract description 2
- 239000002184 metal Substances 0.000 abstract description 2
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 abstract description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 30
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 26
- 239000010955 niobium Substances 0.000 description 17
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 9
- 229910052742 iron Inorganic materials 0.000 description 9
- 239000000463 material Substances 0.000 description 9
- 238000005728 strengthening Methods 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 8
- 229910052720 vanadium Inorganic materials 0.000 description 8
- 230000000694 effects Effects 0.000 description 7
- 238000001556 precipitation Methods 0.000 description 7
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 6
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 5
- 239000011733 molybdenum Substances 0.000 description 5
- FEBJSGQWYJIENF-UHFFFAOYSA-N nickel niobium Chemical compound [Ni].[Nb] FEBJSGQWYJIENF-UHFFFAOYSA-N 0.000 description 5
- 238000010587 phase diagram Methods 0.000 description 5
- 238000004321 preservation Methods 0.000 description 5
- 239000010703 silicon Substances 0.000 description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 229910002804 graphite Inorganic materials 0.000 description 4
- 239000010439 graphite Substances 0.000 description 4
- 229910001068 laves phase Inorganic materials 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 4
- 238000010791 quenching Methods 0.000 description 4
- 230000000171 quenching effect Effects 0.000 description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 3
- 229910000943 NiAl Inorganic materials 0.000 description 3
- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 description 3
- 239000000446 fuel Substances 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 2
- 239000003973 paint Substances 0.000 description 2
- 230000001737 promoting effect Effects 0.000 description 2
- 238000012546 transfer Methods 0.000 description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 229910001093 Zr alloy Inorganic materials 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 230000004888 barrier function Effects 0.000 description 1
- 229910052729 chemical element Inorganic materials 0.000 description 1
- 239000002826 coolant Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000004992 fission Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 229910001256 stainless steel alloy Inorganic materials 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- G—PHYSICS
- 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
- G21C3/06—Casings; Jackets
- G21C3/07—Casings; Jackets characterised by their material, e.g. alloys
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E30/00—Energy generation of nuclear origin
- Y02E30/30—Nuclear fission reactors
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Metallurgy (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Plasma & Fusion (AREA)
- General Engineering & Computer Science (AREA)
- High Energy & Nuclear Physics (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses an Al-containing 20Cr25NiNb austenitic stainless steel for supercritical fluid gas-cooled reactor cladding and a preparation method thereof, wherein the Al-containing austenitic stainless steel comprises the following components in percentage by mass: 19 to 22% of Cr,25 to 27% of Ni,0.02 to 0.06% of C,0.3 to 1.0% of Nb,0.2 to 0.4% of Si,1.8 to 2.5% of Mo,2 to 4% of Al, P < 0.008%, O < 0.003%, and the balance Fe; preferably, the contents of the components are added in an amount of 0.005 to 0.008% by weight B and 0.16 to 0.27% by weight V; an aluminum oxide film is generated between the chromium oxide and the metal matrix by adding Al, so that the corrosion resistance of the stainless steel in a high-temperature supercritical fluid environment is improved; the mass percent of Ni is larger than that of Cr, so that an austenite FCC structure is obtained, and the creep resistance of the alloy in a high-temperature supercritical fluid is greatly improved.
Description
Technical Field
The invention relates to the technical field of iron-based alloy structural materials and special alloy materials, in particular to Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding and a preparation method thereof.
Background
At present, a pressurized water reactor is commonly adopted in domestic nuclear power units, the temperature of a heat source is difficult to increase, and even though the most advanced large water-cooled reactor is adopted, the heat efficiency is just over 40 percent. The Brayton cycle with supercritical fluid as heat transfer medium has compressor operating point and reactor operating point set separately in the great density area and the low density area near the quasi-critical temperature, and can realize the high heat transfer efficiency of gas cooled reactor at medium reactor core outlet temperature and reduce the reactor core volume.
The fuel clad is an important barrier for the reactor, which functions to prevent fission products from escaping, to protect the fuel from corrosion by the coolant, and to efficiently conduct away heat energy. The outlet temperature of the designed reactor core of the supercritical gas cooled reactor system is over 600 ℃, the outlet temperature exceeds the use limit of Zr alloy, and the research and development of novel alloy must be considered.
The main research unit in China develops the material selection work for the advanced gas cooled reactor cladding, and the existing 20Cr25NiNb material has single precipitation strengthening phase at high temperature, so that the strength of the material at 650 ℃ is only 400MPa, and the high-temperature creep property is also low.
Disclosure of Invention
The invention aims to provide Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding, which is 20Cr25NiNb type, so as to solve the problem that the creep property of the existing 20Cr25NiNb type is lower at high temperature.
The invention provides Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding, which comprises the following components in percentage by mass: 19 to 22% of Cr,25 to 27% of Ni,0.02 to 0.06% of C,0.3 to 1.0% of Nb,0.2 to 0.4% of Si,1.8 to 2.5% of Mo,2 to 4% of Al, P < 0.008%, O < 0.003%, and the balance Fe.
The invention has the beneficial effects that: according to the invention, the mass percent of Ni is greater than that of Cr, the content of Cr is controlled to be 19-22%, the mass percent of Ni is increased to more than 25%, and solution treatment and rapid water cooling are carried out at 1150-1250 ℃, as shown in phase diagram analysis (the left graph and the middle graph in figure 1), the obtained stainless steel matrix is ensured to be an austenite FCC structure, and the creep resistance of the stainless steel is effectively improved; when the Cr content reaches 23%, the matrix changes into an austenite FCC structure and a ferrite BCC dual-phase structure (right part of figure 1). The phase diagram (figure 2) shows that the alloy in the composition range of the invention can precipitate a plurality of second phases at high temperature (600-800 ℃), can play a good precipitation strengthening effect and can still have good mechanical properties at the temperature of more than 600 ℃. By adding Al, a layer of compact aluminum oxide film is formed between the chromium-rich oxide layer and the austenite matrix, thereby improving the performance of the stainless steel in supercritical gas (such as supercritical CO) 2 ) Corrosion resistance of the environment.
As a possible implementation mode, the Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding comprises the following components in percentage by mass: 20% of Cr,27% of Ni,0.03% of Nb, 0.8% of Si,2.5% of Mo,3% of Al, P.ltoreq.0.008%, O.ltoreq.0.003%, and the balance Fe.
As a possible implementation mode, the Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding comprises the following components in percentage by mass: 22% Cr,25% Ni,0.06% C,0.8% Nb,0.2% Si,2% Mo,3% Al, P ≦ 0.008%, O ≦ 0.003%, the balance Fe. Phase diagram calculation (in figure 1 and figure 2 c) shows that the alloy is a full austenite structure and trace NbC at 1200 ℃, austenite and a second phase at 600-800 ℃ (the use temperature range of the supercritical fluid gas-cooled reactor cladding), and the precipitation of the second phase plays a good precipitation strengthening role, so that the alloy has better mechanical properties.
As a possible preferred mode, the Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding comprises the following components in percentage by mass: 19-22% of Cr, 25-27% of Ni, 0.02-0.06% of C, 0.3-1.0% of Nb, 0.2-0.4% of Si, 1.8-2.5% of Mo, 2-4% of Al, 0.005-0.008% of B, P ≦ 0.008%, O ≦ 0.003%, the balance Fe; by adding the B element, the problem of coarsening of the Laves second phase at high temperature at the grain boundary caused by adding the Mo element can be inhibited, so that the high-temperature mechanical property of the stainless steel is further improved to a certain extent.
As a possible preferred mode, the Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding comprises the following components in percentage by mass: 19 to 22% of Cr,25 to 27% of Ni,0.02 to 0.06% of C,0.3 to 0.5% of Nb,0.16 to 0.27% of V,0.2 to 0.4% of Si,1.8 to 2.5% of Mo,2 to 4% of Al,0.005 to 0.008% of B, 0.008% of P, 0.003% of O, and the balance of Fe; when the four elements of V, mo, al and B are used cooperatively: v and Nb promote the precipitation of an MC phase (M is Nb or V); mo has the effect of solid solution strengthening, and Fe2Mo type Laves phase can be separated out at 600-800 ℃; promoting NiAl strengthening phase at high temperature of Al; the element B suppresses coarsening of the precipitated phase at the grain boundary, and thus has the effect of strengthening the grain boundary. Promotes the precipitation of phases with good performance under the condition of meeting the phase balance, thereby improving the high-temperature mechanical property and creep resistance of the stainless steel.
As one possible preferred mode, the atomic number ratio of Nb and V is 1.
The invention also discloses a preparation method of the Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding, which comprises the following steps:
mixing the raw materials and smelting into an ingot;
annealing the ingot at 1100-1300 ℃ for 2-3 hours to obtain a steel ingot;
the steel ingot is forged after being subjected to heat preservation for 2 to 3 hours at 1180 to 1220 ℃, and the finish forging temperature is 1050 to 1100 ℃, so that a plate is obtained;
carrying out solution treatment on the plate at 1150-1250 ℃ for 0.5-2 hours, and then cooling the plate to room temperature by water;
and carrying out aging treatment on the plate obtained by the solution treatment at 600-800 ℃ for 500-1000 hours, and then air cooling.
The invention has the beneficial effects that: according to the invention, through the matching of smelting, annealing treatment, forging treatment, solid solution treatment and aging treatment, the second phase is uniformly precipitated and has good dispersion effect, so that the mechanical property of the stainless steel and the structure stability of the stainless steel structure are improved.
As a possible embodiment, the ingot also comprises, before forging, the removal of the scale from the surface of the ingot.
As a possible embodiment, the sheet material further comprises descaling of the surface of the sheet material prior to the solution treatment.
As a possible embodiment, the smelting is carried out in a vacuum smelting furnace with a vacuum degree of 1X 10 -3 ～1×10 -2 Pa。
Drawings
FIG. 1 is a thermodynamic phase diagram of an alloy at 1200 ℃ within the scope of the present invention;
FIG. 2 is a thermodynamic phase diagram of an alloy at 600 deg.C-800 deg.C within the scope of the present invention;
FIG. 3 is an SEM scan of a stainless steel made according to example 1;
FIG. 4 is an SEM scan of a stainless steel made in example 2;
FIG. 5 is an SEM scan of a stainless steel made in example 3;
FIG. 6 is an SEM scan of a stainless steel prepared in comparative example 1;
FIG. 7 is a drawing curve of a stainless steel prepared in example 1;
FIG. 8 is a drawing curve of a stainless steel prepared in example 2;
FIG. 9 is a drawing curve of a stainless steel prepared in example 3;
FIG. 10 is a drawing curve of a stainless steel prepared in comparative example 1.
Detailed Description
In order to make the technical problems, technical solutions and advantageous effects to be solved by the present invention more apparent, the present invention is described in further detail below. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention.
The inventor of the invention finds that the existing gas cooled reactor cladding material 20Cr25NiNb stainless steel has single precipitated phase and insufficient creep resistance at high temperature (600-800 ℃), so that the existing gas cooled reactor cladding material is not suitable for the supercritical fluid environment.
The inventor of the invention finds that Al is added into the 20Cr25NiNb fuel cladding material to generate an alumina film between chromium oxide and a metal matrix, thereby improving the corrosion resistance of stainless steel in a high-temperature (600-800 ℃) supercritical fluid environment; by controlling the addition amount of alloy elements, particularly meeting the condition that the mass percent of Ni is more than that of Cr, and controlling the mass percent of Cr and Ni between 19-22% and 25-27% respectively, the stainless steel matrix after solution treatment is of an austenite FCC structure, and simultaneously, aging treatment at high temperature (600-800 ℃) is matched to precipitate a large amount of second phases, so that the creep resistance and the mechanical property of the alloy in a high-temperature supercritical fluid environment are greatly improved.
The invention discloses Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding, which comprises the following components in percentage by mass: 19 to 22% of Cr,25 to 27% of Ni,0.02 to 0.06% of C,0.3 to 1.0% of Nb,0.2 to 0.4% of Si,1.8 to 2.5% of Mo,2 to 4% of Al, P < 0.008%, O < 0.003%, and the balance Fe.
As used herein, the term "supercritical fluid" refers to a fluid above the critical temperature and critical pressure that has no significant gas-liquid interface.
As used herein, the term "elevated temperature" means 600 to 800 ℃.
In the invention, in order to avoid that the matrix becomes ferrite after Al is added, the mass percent of Ni is adjusted to be larger than that of Cr, and the mass percent of Ni is controlled to be more than 25 percent, thereby ensuring that the matrix is still austenite under the condition of high temperature and has good creep resistance; by controlling the addition of Cr with higher content and a certain amount of Al element, the structure of an austenite matrix-aluminum oxide film-chromium oxide layer from inside to outside is realized, and the corrosion resistance is improved.
In the invention, the Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding suitably comprises the following components in percentage by mass: 20% of Cr,27% of Ni,0.03% of Nb, 0.8% of Si,2.5% of Mo,3% of Al, P.ltoreq.0.008%, O.ltoreq.0.003%, the balance being Fe; suitably, the Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding comprises the following components in percentage by mass: 22% Cr,25% Ni,0.06% C,0.8% Nb,0.2% Si,3% Mo,3% Al, P.ltoreq.0.008%, O.ltoreq.0.003%, the remainder being Fe.
On the basis of adding Mo, a Laves second phase is formed in the stainless steel alloy, and in order to inhibit the coarsening problem of the Laves second phase at high temperature of a grain boundary caused by Mo, the B element is added to inhibit the coarsening of the Laves second phase, so that the crystal grains of the second phase are fine and uniform, and the high-temperature mechanical property of the stainless steel is improved.
After the element B is added, the Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding can be prepared as follows: the paint comprises the following components in percentage by mass: 19-22% Cr, 25-27% Ni, 0.02-0.06% C, 0.3-1.0% Nb, 0.2-0.4% Si, 1.8-2.5% Mo, 2-4% Al, 0.005-0.008% B, P ≦ 0.008%, O ≦ 0.003%, the balance Fe.
In the invention, V element can be added to replace a part of Nb element, and the two elements can cooperate to further improve the mechanical property of the stainless steel; suitably, the composition of the Al-containing austenitic stainless steel for supercritical fluid gas cooled reactor cladding may be as follows: the paint comprises the following components in percentage by mass: 19 to 22% of Cr,25 to 27% of Ni,0.02 to 0.06% of C,0.3 to 0.5% of Nb,0.16 to 0.27% of V,0.2 to 0.4% of Si,1.8 to 2.5% of Mo,2 to 4% of Al,0.005 to 0.008% of B, 0.008% of P, 0.003% of O, and the balance of Fe; more suitably, the atomic number ratio of Nb and V is 1.
In the invention, when four elements of V, mo, al and B are used cooperatively, V and Nb promote MC phase (M is Nb or V) to be precipitated together; mo has the effect of solid solution strengthening, and Fe2Mo type Laves phases can be separated out at 600-800 ℃; promoting NiAl strengthening phase at high temperature of Al; the element B suppresses coarsening of a precipitated phase at grain boundaries, and thus has an effect of strengthening the grain boundaries. Promotes the precipitation of phases with good performance under the condition of meeting the phase balance, thereby improving the high-temperature mechanical property and creep resistance of the stainless steel.
The invention also discloses a preparation method of the Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding, which comprises the following steps:
s1, mixing the raw materials and then smelting into an ingot;
in the present invention, the melting may be carried out in a vacuum melting furnace having a vacuum degree of generally 1X 10 -3 ～1×10 -2 Pa, suitably 5X 10 -3 ～1×10 -2 Pa。
S2, annealing the ingot at 1100-1300 ℃ for 2-3 hours to obtain a steel ingot;
in the present invention, suitably, the annealing temperature is 1200 ± 20 ℃, more suitably 1200 ℃.
S3, forging the steel ingot after heat preservation is carried out for 2-3 hours at 1180-1220 ℃, wherein the finish forging temperature is 1050-1100 ℃, and obtaining a plate;
in the present invention, suitably, 1200 ℃; in the present invention, the finish forging temperature is suitably 1080 to 1100 ℃, more suitably 1100 ℃.
S4, carrying out solid solution treatment on the plate at 1150-1250 ℃ for 0.5-2 hours, and then cooling the plate to room temperature by water;
in the present invention, the temperature of the solid solution is suitably 1200 ± 20 ℃, more suitably 1200 ℃.
In the invention, the water cooling mode can be that the plate is placed in a container filled with water for soaking and cooling so as to shorten the time required by cooling.
S5, carrying out aging treatment on the plate obtained by the solution treatment at 600-800 ℃ for 500-1000 hours, and then air cooling.
The invention ensures that the finally obtained austenitic stainless steel has more uniform and fine grain structure by the mutual matching of the steps, and avoids C element from forming M 23 C 6 The possibility of intergranular corrosion is reduced, and the mechanical property and the structure stability of the stainless steel are improved.
Examples
In the following examples, the Fe source, ni source, cr source, nb source, si source, mo source, al source, V source, B source, and C source are commercially pure iron (99.6 wt%), commercially pure nickel (99.95 wt%), commercially pure chromium (99.95 wt%), nickel-niobium (62 wt%) master alloy, commercially pure silicon, commercially pure molybdenum bar, commercially pure aluminum, high-purity vanadium powder (99.5 wt%), boron (22 wt%) iron master alloy, and graphitic carbon, respectively, and the rest of the raw materials are conventionally selected, but not listed here.
Example 1
The austenitic stainless steel for supercritical fluid gas cooled reactor cladding contains the elements shown in table 1.
The preparation steps of the austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding disclosed by the embodiment are as follows:
s1, 10.2kg of industrial pure iron, 4.8kg of industrial pure nickel, 4kg of industrial pure chromium, 242g of nickel-niobium intermediate alloy, 40g of industrial pure silicon, 400g of industrial pure molybdenum, 580g of industrial pure aluminum and 8g of graphite carbon are mixed and added into a furnace with the vacuum degree of 1 multiplied by 10 -3 Smelting in a vacuum smelting furnace of Pa for 2 hours to obtain an ingot 1;
s2, annealing the ingot 1 at the target temperature of 1100 ℃ for 2 hours to obtain a steel ingot 1;
s3, forging the steel ingot 1 after heat preservation is carried out for 2 hours at a target temperature of 1180 ℃, wherein the target temperature of finish forging is 1050 ℃, and obtaining a plate 1;
s4, carrying out solid solution treatment on the plate 1 at a target temperature of 1150 ℃ for 3 hours, and then quenching in water;
s5, carrying out aging treatment on the plate 1 subjected to the solution treatment at the target temperature of 600 ℃ for 1.2h, and then carrying out air cooling.
Example 2
The austenitic stainless steel for supercritical fluid gas-cooled reactor cladding contains the elements shown in table 1.
The preparation steps of the austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding disclosed by the embodiment are as follows:
s1, 10.3kg of industrial pure iron, 4.8kg of industrial pure nickel, 4kg of industrial pure chromium, 240g of nickel-niobium intermediate alloy, 40g of industrial pure silicon, 400g of industrial pure molybdenum, 580g of industrial pure aluminum, 6g of boron (22 wt%) iron intermediate alloy and 9g of graphite carbon are mixed and added into a mixture with the vacuum degree of 5 x 10 -3 Smelting in a vacuum smelting furnace of Pa for 3 hours to obtain an ingot 2;
s2, annealing the ingot 2 at the target temperature of 1200 ℃ for 3 hours to obtain a steel ingot 2;
s3, keeping the temperature of the steel ingot 2 at 1200 ℃ for 3 hours, and then forging, wherein the target temperature of finish forging is 1100 ℃, so as to obtain a plate 2;
s4, carrying out solid solution treatment on the plate 2 at the target temperature of 1200 ℃ for 3 hours, and then quenching in water;
s5, carrying out aging treatment on the plate 2 subjected to the solution treatment at the target temperature of 700 ℃ for 0.8h, and then cooling in air.
Example 3
The austenitic stainless steel for supercritical fluid gas-cooled reactor cladding contains the elements shown in table 1.
The preparation steps of the austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding disclosed by the embodiment are as follows:
s1, 10.3kg of industrial pure iron, 5kg of industrial pure nickel, 4.3kg of industrial pure chromium, 140g of nickel-niobium intermediate alloy, 45g of industrial pure silicon, 400g of industrial pure molybdenum, 620g of industrial pure aluminum, 70g of high-purity vanadium powder, 6g of boron (22 wt%) iron intermediate alloy and 7g of graphite carbon are mixed and added into a furnace with the vacuum degree of 1 x 10 -2 Smelting in a vacuum smelting furnace of Pa for 3 hours to obtain an ingot 3;
s2, annealing the ingot 3 at the target temperature of 1300 ℃ for 2 hours to obtain a steel ingot 3;
s3, performing heat preservation on the steel ingot 3 at a target temperature of 1200 ℃ for 3 hours, and then forging, wherein the target temperature of finish forging is 1050 ℃, so as to obtain a plate 3;
s4, carrying out solid solution treatment on the plate 3 at the target temperature of 1250 ℃ for 0.5 hour, and then quenching in water;
s5, carrying out aging treatment on the plate 3 subjected to the solution treatment at the target temperature of 800 ℃ for 1 hour, and then carrying out air cooling.
Comparative example 1
The Al-free 20Cr25NiNb austenitic stainless steel contains the elements shown in Table 1.
The preparation method of the 20Cr25NiNb austenitic stainless steel comprises the following steps:
s1, 10.5kg of industrial pure iron, 4.8kg of industrial pure nickel, 4kg of industrial pure chromium, 220g of nickel-niobium intermediate alloy, 42g of industrial pure silicon, 420g of industrial pure molybdenum and 9.5g of graphite carbon are mixed and added into a furnace with the vacuum degree of 1 multiplied by 10 -3 Smelting in a vacuum smelting furnace of Pa for 2 hours to obtain an ingot 4;
s2, annealing the ingot 4 at the target temperature of 1100 ℃ for 2 hours to obtain a steel ingot 4;
s3, performing heat preservation on the steel ingot 4 at a target temperature of 1180 ℃ for 2 hours, and then forging, wherein the target temperature of finish forging is 1050 ℃, so as to obtain a plate 4;
s4, carrying out solid solution treatment on the plate 4 at a target temperature of 1150 ℃ for 3 hours, and then quenching in water;
s5, carrying out aging treatment on the plate 4 subjected to the solution treatment at a target temperature of 600 ℃ for 1.2h, and then cooling in air.
The compositions of the stainless steels prepared in examples 1 to 3 and comparative example 1 are shown in table 1, and the following tables are mass percentages.
TABLE 1
It should be noted that: "bal." is an abbreviation for "banlane" in table 1, meaning that, in addition to other chemical elements, a mass percentage of Fe remains.
SEM scans of the stainless steels prepared in examples 1 to 3 and comparative example 1 are sequentially shown in fig. 3 to 6, and it can be seen from fig. 3 to 6 that,
in the SEM scans of examples 1-3, after aging at 650 ℃ for 1000 hours, a large amount of black needle-like precipitates (NiAl phase) and white precipitates (Laves phase and MC phase) are dispersed in the grain and in the grain boundary, and particularly, after the B element and the V element are added (example 3), a large amount of fine dispersed second phase is precipitated, so that the high-temperature mechanical strength level is greatly improved. In contrast, in comparative example 1, almost no precipitates were observed in the grains, and only a small amount of discontinuous white Laves phase was distributed in the grain boundaries, whereby it was found that the addition of Al, V and B was advantageous for improving the high-temperature mechanical properties of stainless steel.
The stainless steels obtained in examples 1 to 3 and comparative example 1 were subjected to an air tensile test at 650 ℃ and the tensile curves are shown in the sequence of fig. 7 to 10, and the tensile strength results are shown in table 2.
TABLE 2
As can be seen from fig. 7-10 and table 2, examples 1 to 3 all have good high-temperature mechanical strength levels, and particularly, the high-temperature mechanical strength is greatly improved after the B element and the V element are added.
As can be seen from comparison of examples 1-3 with comparative example 1, the stainless steel containing no Al/V/B/Mo element had a poor strength level at 650 ℃ which was only about half of that of the stainless steels prepared in examples 1-3.
The above-mentioned embodiments, objects, technical solutions and advantages of the present invention are further described in detail, it should be understood that the above-mentioned embodiments are only examples 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 Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding is characterized by comprising the following components in percentage by mass: 19 to 22% of Cr,25 to 27% of Ni,0.02 to 0.06% of C,0.3 to 1.0% of Nb,0.2 to 0.4% of Si,1.8 to 2.5% of Mo,2 to 4% of Al, P < 0.008%, O < 0.003%, and the balance Fe.
2. The Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding according to claim 1, is characterized by comprising the following components in percentage by mass: 20% of Cr,27% of Ni,0.03% of Nb, 0.8% of Si,2.5% of Mo,3% of Al, P.ltoreq.0.008%, O.ltoreq.0.003%, and the balance Fe.
3. The Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding according to claim 1, is characterized by comprising the following components in percentage by mass: 22% Cr,25% Ni,0.06% C,0.8% Nb,0.2% Si,2% Mo,3% Al, P.ltoreq.0.008%, O.ltoreq.0.003%, the remainder being Fe.
4. The Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding according to claim 1, is characterized by comprising the following components by mass percent: 19 to 22% of Cr,25 to 27% of Ni,0.02 to 0.06% of C,0.3 to 1.0% of Nb,0.2 to 0.4% of Si,1.8 to 2.5% of Mo,2 to 4% of Al,0.005 to 0.008% of B, P < 0.008%, O < 0.003%, and the balance of Fe.
5. The Al-containing austenitic stainless steel for the supercritical fluid gas-cooled reactor cladding according to claim 1, is characterized by comprising the following components in percentage by mass: 19-22% Cr, 25-27% Ni, 0.02-0.06% C, 0.3-0.5% Nb, 0.16-0.27% by weight V, 0.2-0.4% by weight Si, 1.8-2.5% Mo, 2-4% by weight Al, 0.005-0.008% by weight B, P ≦ 0.008%, O ≦ 0.003%, the balance Fe.
6. The Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding according to claim 5, wherein the atomic number ratio of Nb to V is 1.
7. A method of manufacturing the Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding according to any of claims 1-6, characterized in that the method of manufacturing comprises the steps of:
mixing the raw materials and smelting into an ingot;
annealing the ingot at 1100-1300 ℃ for 2-3 hours to obtain a steel ingot;
keeping the temperature of the steel ingot at 1180-1220 ℃ for 2-3 hours, and then forging the steel ingot, wherein the finish forging temperature is 1050-1100 ℃, so as to obtain a plate;
carrying out solid solution treatment on the plate at 1150-1250 ℃ for 0.5-2 hours, and then cooling the plate to room temperature by water;
and carrying out aging treatment on the plate obtained by the solution treatment at 600-800 ℃ for 500-1000 hours, and then air cooling.
8. A method of making according to claim 7, wherein the steel ingot further comprises removing scale from the surface of the steel ingot prior to forging.
9. The method of claim 7, wherein the sheet further comprises descaling the surface of the sheet prior to solution treatment.
10. The production method according to claim 7, wherein the melting is performed in a vacuum melting furnace having a degree of vacuum of 1 x 10 -3 ～1×10 -2 Pa。
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210900087.2A CN115233107A (en) | 2022-07-28 | 2022-07-28 | Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210900087.2A CN115233107A (en) | 2022-07-28 | 2022-07-28 | Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN115233107A true CN115233107A (en) | 2022-10-25 |
Family
ID=83678277
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210900087.2A Pending CN115233107A (en) | 2022-07-28 | 2022-07-28 | Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115233107A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115595511A (en) * | 2022-10-26 | 2023-01-13 | 四川大学（Cn） | Aluminum-containing austenitic stainless steel resistant to liquid lead and bismuth corrosion and preparation method thereof |
| CN116288029A (en) * | 2023-01-06 | 2023-06-23 | 清华大学 | Light ultra-high strength austenitic stainless steel and preparation method thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1391517A (en) * | 1999-11-30 | 2003-01-15 | 克鲁普德国联合金属制造有限公司 | Production of heat resistant alloy with good high temperature oxidation resistance |
| CN107075629A (en) * | 2014-09-19 | 2017-08-18 | 新日铁住金株式会社 | Austenite stainless steel plate |
| CN108474072A (en) * | 2016-01-05 | 2018-08-31 | 新日铁住金株式会社 | Austenitic heat-resistant alloy and its manufacturing method |
| CN113151747A (en) * | 2021-04-27 | 2021-07-23 | 中国核动力研究设计院 | High-temperature corrosion resistant aluminum-containing austenitic stainless steel and preparation method thereof |
| CN114318169A (en) * | 2021-11-16 | 2022-04-12 | 上海交通大学 | Aluminum-containing austenitic stainless steel resistant to supercritical water/supercritical carbon dioxide corrosion |
-
2022
- 2022-07-28 CN CN202210900087.2A patent/CN115233107A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1391517A (en) * | 1999-11-30 | 2003-01-15 | 克鲁普德国联合金属制造有限公司 | Production of heat resistant alloy with good high temperature oxidation resistance |
| CN107075629A (en) * | 2014-09-19 | 2017-08-18 | 新日铁住金株式会社 | Austenite stainless steel plate |
| CN108474072A (en) * | 2016-01-05 | 2018-08-31 | 新日铁住金株式会社 | Austenitic heat-resistant alloy and its manufacturing method |
| CN113151747A (en) * | 2021-04-27 | 2021-07-23 | 中国核动力研究设计院 | High-temperature corrosion resistant aluminum-containing austenitic stainless steel and preparation method thereof |
| CN114318169A (en) * | 2021-11-16 | 2022-04-12 | 上海交通大学 | Aluminum-containing austenitic stainless steel resistant to supercritical water/supercritical carbon dioxide corrosion |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115595511A (en) * | 2022-10-26 | 2023-01-13 | 四川大学（Cn） | Aluminum-containing austenitic stainless steel resistant to liquid lead and bismuth corrosion and preparation method thereof |
| CN116288029A (en) * | 2023-01-06 | 2023-06-23 | 清华大学 | Light ultra-high strength austenitic stainless steel and preparation method thereof |
| CN116288029B (en) * | 2023-01-06 | 2023-09-05 | 清华大学 | Light ultra-high strength austenitic stainless steel and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN115233107A (en) | Al-containing austenitic stainless steel for supercritical fluid gas-cooled reactor cladding and preparation method thereof | |
| CN101906595B (en) | Austenite heat-resistance stainless steel forming Al2O3 protective layer spontaneously | |
| US4963200A (en) | Dispersion strengthened ferritic steel for high temperature structural use | |
| CN108779538B (en) | High-strength Fe-Cr-Ni-Al multi-phase stainless steel and manufacturing method thereof | |
| CN115233105B (en) | Austenitic stainless steel alloy for supercritical gas-cooled reactor fuel cladding and preparation method thereof | |
| CN112981210B (en) | Nuclear medium-entropy alloy system and preparation method and application thereof | |
| CN108642373A (en) | A kind of high-temperature oxidation resistant austenitic heat-resistance steel and its preparation process | |
| CN111893365B (en) | Carbon-containing FeMnNiAlCr high-entropy alloy and preparation method thereof | |
| CN114351028B (en) | One kind (FeVCrMn) x Ti y Low-activation high-entropy alloy and preparation method thereof | |
| CN109652628A (en) | A kind of used by nuclear fuel jacketing FeCrAl alloy and its preparation and crystallite dimension control method | |
| CN109763066A (en) | A kind of ultra-high parameter steam turbine key hot-end component New Heat-Resistant Steel | |
| CN106995902A (en) | A kind of FeCrAl based alloys cladding materials and preparation method thereof | |
| US6761854B1 (en) | Advanced high temperature corrosion resistant alloy | |
| CN116426725B (en) | 15-5 Stainless steel modification method and product prepared by same | |
| JPH01287252A (en) | Sintered dispersion strengthened ferritic heat-resistant steel | |
| CN107142423B (en) | A kind of crash-proof nuclear fuel assembly structural material FeCrAl based alloy and preparation method thereof | |
| CN115491600A (en) | Ferrite/martensite heat-resistant steel for lead-bismuth pile and preparation method thereof | |
| CN115354227A (en) | Ferrite martensitic steel for reactor fuel cladding material and heat treatment process thereof | |
| CN111304555B (en) | In-situ endogenously precipitated ceramic particle reinforced Cr-Mn-Ni-C-N austenitic heat-resistant steel and preparation method and application thereof | |
| CN111826590B (en) | Fe23Zr6And Fe2M-Laves phase co-reinforced FeCrAl stainless steel and preparation method thereof | |
| CN111705195B (en) | Precipitation strengthening heat treatment process for Nb-containing austenitic heat-resistant steel | |
| CN116162852B (en) | High-strength corrosion-resistant austenitic heat-resistant steel for cores, and preparation method and application thereof | |
| CN114540693A (en) | High-strength, high-toughness and corrosion-resistant Fe-rich Si-containing multi-component alloy and preparation method and application thereof | |
| CN107236904A (en) | A kind of nuclear reactor FeCrAl base alloy materials and preparation method thereof | |
| KR101507898B1 (en) | super heat resistant alloy and the manufacturing method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20221025 |