CN115948693A - Corrosion-resistant steel, preparation method and application thereof, and crude oil storage tank - Google Patents
Corrosion-resistant steel, preparation method and application thereof, and crude oil storage tank Download PDFInfo
- Publication number
- CN115948693A CN115948693A CN202211225169.8A CN202211225169A CN115948693A CN 115948693 A CN115948693 A CN 115948693A CN 202211225169 A CN202211225169 A CN 202211225169A CN 115948693 A CN115948693 A CN 115948693A
- Authority
- CN
- China
- Prior art keywords
- corrosion
- steel
- resistant steel
- rolling
- temperature
- 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
- 239000010935 stainless steel Substances 0.000 title claims abstract description 67
- 239000010779 crude oil Substances 0.000 title claims abstract description 22
- 238000003860 storage Methods 0.000 title claims abstract description 22
- 238000002360 preparation method Methods 0.000 title claims abstract description 19
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 119
- 239000010959 steel Substances 0.000 claims abstract description 119
- 238000003466 welding Methods 0.000 claims abstract description 60
- 238000004519 manufacturing process Methods 0.000 claims abstract description 6
- 238000005096 rolling process Methods 0.000 claims description 57
- 238000001816 cooling Methods 0.000 claims description 29
- 239000002245 particle Substances 0.000 claims description 27
- 229910052799 carbon Inorganic materials 0.000 claims description 25
- 238000005266 casting Methods 0.000 claims description 24
- 229910052757 nitrogen Inorganic materials 0.000 claims description 23
- 229910052720 vanadium Inorganic materials 0.000 claims description 22
- 238000000034 method Methods 0.000 claims description 19
- 238000010438 heat treatment Methods 0.000 claims description 18
- 229910052719 titanium Inorganic materials 0.000 claims description 17
- 230000009467 reduction Effects 0.000 claims description 13
- 238000005496 tempering Methods 0.000 claims description 13
- 239000002131 composite material Substances 0.000 claims description 10
- 229910045601 alloy Inorganic materials 0.000 claims description 9
- 239000000956 alloy Substances 0.000 claims description 9
- 239000002994 raw material Substances 0.000 claims description 9
- 229910052760 oxygen Inorganic materials 0.000 claims description 8
- 229910052717 sulfur Inorganic materials 0.000 claims description 8
- 239000000203 mixture Substances 0.000 claims description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 5
- 239000000126 substance Substances 0.000 claims description 4
- 230000004927 fusion Effects 0.000 claims description 3
- 239000000463 material Substances 0.000 claims description 3
- 229910052729 chemical element Inorganic materials 0.000 claims 1
- 238000005260 corrosion Methods 0.000 abstract description 63
- 230000007797 corrosion Effects 0.000 abstract description 61
- 230000001976 improved effect Effects 0.000 abstract description 14
- 238000007670 refining Methods 0.000 description 23
- 229910000859 α-Fe Inorganic materials 0.000 description 20
- 230000000052 comparative effect Effects 0.000 description 17
- 239000010936 titanium Substances 0.000 description 16
- 238000011282 treatment Methods 0.000 description 16
- 230000008569 process Effects 0.000 description 14
- 229910001566 austenite Inorganic materials 0.000 description 12
- 239000002893 slag Substances 0.000 description 12
- 238000012360 testing method Methods 0.000 description 12
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 11
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 10
- 230000002829 reductive effect Effects 0.000 description 10
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 9
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 8
- 238000010586 diagram Methods 0.000 description 8
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 7
- 238000005275 alloying Methods 0.000 description 7
- 230000015572 biosynthetic process Effects 0.000 description 7
- 239000011572 manganese Substances 0.000 description 7
- 238000004088 simulation Methods 0.000 description 7
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 6
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 6
- 239000011575 calcium Substances 0.000 description 6
- 239000010949 copper Substances 0.000 description 6
- 239000013078 crystal Substances 0.000 description 6
- 229910052748 manganese Inorganic materials 0.000 description 6
- 239000011159 matrix material Substances 0.000 description 6
- 230000006911 nucleation Effects 0.000 description 6
- 238000010899 nucleation Methods 0.000 description 6
- 239000010703 silicon Substances 0.000 description 6
- 229910052710 silicon Inorganic materials 0.000 description 6
- 229910052684 Cerium Inorganic materials 0.000 description 5
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 5
- 229910052746 lanthanum Inorganic materials 0.000 description 5
- 239000000243 solution Substances 0.000 description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 4
- 238000003723 Smelting Methods 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 4
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 4
- 229910052802 copper Inorganic materials 0.000 description 4
- 230000003009 desulfurizing effect Effects 0.000 description 4
- 239000011777 magnesium Substances 0.000 description 4
- 229910052759 nickel Inorganic materials 0.000 description 4
- 239000001301 oxygen Substances 0.000 description 4
- 238000005204 segregation Methods 0.000 description 4
- 239000011593 sulfur Substances 0.000 description 4
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 3
- 229910001200 Ferrotitanium Inorganic materials 0.000 description 3
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 3
- 239000002253 acid Substances 0.000 description 3
- 230000002378 acidificating effect Effects 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 229910052791 calcium Inorganic materials 0.000 description 3
- 239000010941 cobalt Substances 0.000 description 3
- 229910017052 cobalt Inorganic materials 0.000 description 3
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000002474 experimental method Methods 0.000 description 3
- 238000007654 immersion Methods 0.000 description 3
- 229910052749 magnesium Inorganic materials 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 239000011733 molybdenum Substances 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 2
- 229910000519 Ferrosilicon Inorganic materials 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- 239000006004 Quartz sand Substances 0.000 description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 2
- SKKMWRVAJNPLFY-UHFFFAOYSA-N azanylidynevanadium Chemical class [V]#N SKKMWRVAJNPLFY-UHFFFAOYSA-N 0.000 description 2
- 229910001563 bainite Inorganic materials 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000005530 etching Methods 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- 230000036961 partial effect Effects 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 230000001681 protective effect Effects 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 2
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 239000003513 alkali Substances 0.000 description 1
- 239000011324 bead Substances 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000001939 inductive effect Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 238000007689 inspection Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 230000003211 malignant effect Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- MEFBJEMVZONFCJ-UHFFFAOYSA-N molybdate Chemical compound [O-][Mo]([O-])(=O)=O MEFBJEMVZONFCJ-UHFFFAOYSA-N 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 229910017464 nitrogen compound Inorganic materials 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 239000003208 petroleum Substances 0.000 description 1
- 238000004321 preservation Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000000746 purification Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 1
- 239000011573 trace mineral Substances 0.000 description 1
- 235000013619 trace mineral Nutrition 0.000 description 1
- 230000004580 weight loss Effects 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Images
Classifications
-
- 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
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
The invention belongs to the technical field of steel preparation, and particularly relates to corrosion-resistant steel, a preparation method and application thereof, and a crude oil storage tank. According to the invention, the components and the proportion in the steel are optimized, so that the obtained steel has excellent corrosion resistance; and after the large heat input welding is carried out, the obtained welding heat affected zone has excellent toughness, so that the production efficiency and the service life of the crude oil storage tank prepared from steel can be improved.
Description
Technical Field
The invention belongs to the technical field of steel preparation, and particularly relates to corrosion-resistant steel, a preparation method and application thereof, and a crude oil storage tank.
Background
In the preparation process of the crude oil storage tank, in order to improve the welding efficiency, the large heat input welding is mainly adopted, and the welding heat input can reach 100kJ/cm. During high heat input welding, because the temperature of a welding heat affected zone is as high as 1400 ℃, austenite grains are obviously grown, coarse grain boundary ferrite is formed in the subsequent cooling process, the intragranular structure is deteriorated, and the toughness of the welding heat affected zone is reduced.
Therefore, when the steel for the crude oil storage tank is designed, the steel has good corrosion resistance in an acid corrosion environment with high sulfur content; meanwhile, the steel has good welding performance under the condition of large heat input welding.
Chinese patents CN102242309A and CN101215669A both disclose a steel for crude oil storage tank for large heat input welding, which improves the toughness of the welding heat affected zone formed by large heat input welding and improves the welding performance by adjusting the components of the steel, but the corrosion resistance of the steel itself is reduced, resulting in the reduction of the service life of the crude oil storage tank.
Disclosure of Invention
The invention aims to provide corrosion-resistant steel, a preparation method and application thereof and a crude oil storage tank.
In order to achieve the above purpose, the invention provides the following technical scheme:
the invention provides corrosion-resistant steel which comprises the following components in percentage by mass: c:0.03 to 0.07%, si: 0.06-0.25%, mn: 0.5-1.35%, P is less than or equal to 0.012%, S is less than or equal to 0.005%, cu:0.1 to 0.4%, ni: 0.1-0.5%%, mo:0.10 to 0.30%, V:0.01 to 0.05%, ti: 0.005-0.035%, sn:0.01 to 0.06%, ce:0.001 to 0.03%, la:0.001 to 0.03%, ca:0.0002 to 0.005%, mg:0.0002 to 0.001%, zr:0.001 to 0.02%, co: 0.005-0.3%, O is less than or equal to 0.0030%, N:0.0045 to 0.0065 percent of the total weight of the alloy, and the balance of Fe and inevitable impurities;
wherein, the mass percentage content of Ti, V, C and N satisfies 0.04 ≤ 2.35Ti +0.31V +0.02C +0.02N ≤ 0.06.
The invention also provides a preparation method of the corrosion-resistant steel, which comprises the following steps:
heating, rough rolling, finish rolling, cooling and tempering the casting blank in sequence to obtain the corrosion-resistant steel;
the chemical components of the casting blank are consistent with those of the corrosion-resistant steel in the technical scheme.
Preferably, the heating temperature is 1190-1210 ℃, and the heat preservation time is 9-16 min/cm.
Preferably, the rolling temperature of the rough rolling is 1050-1090 ℃;
the rough rolling is multi-pass rolling, and the maximum reduction rate of a single pass is more than or equal to 10%.
Preferably, the rolling temperature of the finish rolling is 800-930 ℃;
the initial rolling temperature of the finish rolling is 900-930 ℃, and the final rolling temperature is 810-840 ℃;
the finish rolling is multi-pass rolling, and the maximum reduction rate of a single pass is more than or equal to 10%.
Preferably, the cooling starting temperature is 760-800 ℃, and the cooling rate is more than or equal to 6 ℃/s;
the temperature of the return red of the casting blank obtained after cooling is 530-570 ℃.
Preferably, the tempering temperature is 500 to 650 ℃.
The invention also provides application of the corrosion-resistant steel in the technical scheme or the corrosion-resistant steel prepared by the preparation method in the technical scheme in a crude oil storage tank.
The invention also provides a crude oil storage tank which is prepared by welding steel serving as a raw material, wherein the steel is the corrosion-resistant steel in the technical scheme or the corrosion-resistant steel prepared by the preparation method in the technical scheme.
Preferably, the welding is high heat input welding;
the welded joint formed by welding comprises a weld zone, a fusion zone and a welding heat affected zone;
among the precipitated particles with the size of 20-80 nm in the welding heat affected zone, the number of (V, ti) (C, N) composite precipitated particles accounts for 60-70%;
the number of (Ti, V) (C, N) composite precipitated particles in the weld heat affected zone is 60-70% of precipitated particles having a size of 0.5-1.5 [ mu ] m.
The invention provides corrosion-resistant steel which comprises the following components in percentage by mass: c:0.03 to 0.07%, si: 0.06-0.25%, mn: 0.5-1.35%, P is less than or equal to 0.012%, S is less than or equal to 0.005%, cu:0.1 to 0.4%, ni: 0.1-0.5%, mo:0.10 to 0.30%, V:0.01 to 0.05%, ti: 0.005-0.035%, sn:0.01 to 0.06 percent, ce:0.001 to 0.03%, la:0.001 to 0.03%, ca:0.0002 to 0.005%, mg:0.0002 to 0.001%, zr:0.001 to 0.02%, co: 0.005-0.3%, O is less than or equal to 0.0030%, N:0.0045 to 0.0065 percent of the total weight of the alloy, and the balance of Fe and inevitable impurities; wherein, the mass percentage content of Ti, V, C and N satisfies 0.04 ≤ 2.35Ti +0.31V +0.02C +0.02N ≤ 0.06. According to the invention, sn and Ce are added into a basic alloy system, and the Sn can generate a stable corrosion layer in an acid environment, so that the corrosion rate is slowed down; ce slows down the pitting rate by modifying the inclusions and improves the corrosion resistance of the steel plate. By adding the trace elements Nb, V and Ti, the formation of second phase particles in a heat affected zone can be promoted, small-size particles can pin austenite crystal boundaries, and large-size particles can promote the formation of acicular ferrite. Under the synergistic action of all elements, the corrosion-resistant steel provided by the invention has excellent corrosion resistance; meanwhile, after large heat input welding is carried out, the obtained welding heat affected zone has excellent toughness, and the service life of the crude oil storage tank prepared from the corrosion-resistant steel is prolonged.
Drawings
FIG. 1 is a metallographic structure diagram of a macrocrystalline heat affected zone obtained by a weld heat simulation experiment performed on the corrosion-resistant steel obtained in example 4;
FIG. 2 is a metallographic structure diagram of a coarse grain heat affected zone obtained by performing a welding heat simulation experiment on the corrosion-resistant steel obtained in comparative example 1;
FIG. 3 is a diagram of an apparatus for performing corrosion resistance tests according to an embodiment of the present invention, wherein 1-water bath heating, 2-beaker, 3-etching solution, 4-coupon sample, 5-water;
fig. 4 is a diagram showing the corrosion-resistant steels obtained in example 1 and comparative example 1 after corrosion.
Detailed Description
The invention provides corrosion-resistant steel which comprises the following components in percentage by mass: c:0.03 to 0.07%, si: 0.06-0.25%, mn: 0.5-1.35%, P is less than or equal to 0.012%, S is less than or equal to 0.005%, cu:0.1 to 0.4%, ni: 0.1-0.5%, mo:0.10 to 0.30%, V:0.01 to 0.05%, ti: 0.005-0.035%, sn:0.01 to 0.06%, ce:0.001 to 0.03%, la:0.001 to 0.03%, ca:0.0002 to 0.005%, mg:0.0002 to 0.001%, zr:0.001 to 0.02%, co: 0.005-0.3%, O is less than or equal to 0.0030%, N:0.0045 to 0.0065 percent of Fe and the balance of inevitable impurities;
wherein, the mass percentage content of Ti, V, C and N satisfies 0.04 ≤ 2.35Ti +0.31V +0.02C +0.02N ≤ 0.06.
The corrosion-resistant steel provided by the invention comprises C.03-0.07%, more preferably 0.04-0.06%, and even more preferably 0.045-0.05% by mass. In the invention, carbon is used as a main strengthening element of the corrosion-resistant steel, if the content of the carbon is too high, segregation is generated, so that the corrosion resistance of the whole steel is reduced; meanwhile, the carbon equivalent is increased, the M-A island component is not beneficial to refining, the toughness of a welding heat affected zone formed by large heat input welding is reduced, and the welding crack sensitivity is increased. The invention controls the content of carbon in the range, and can improve the corrosion resistance of steel while ensuring the mechanical property and welding property of the steel.
The corrosion-resistant steel provided by the invention comprises 0.06-0.25% of Si, more preferably 0.08-0.22%, and even more preferably 0.10-0.20% by mass. In the invention, by adding the silicon element into the steel, the silicon element can be dissolved in ferrite and austenite, thereby improving the hardness and strength of the steel and making up for partial strength loss caused by reducing the carbon content; meanwhile, the silicon element can improve the compactness of a steel matrix rust layer and the chemical stability of the rust layer and enhance the corrosion resistance of steel. However, if the addition amount of silicon is too high, nucleation of grain boundary ferrite is promoted, formation of acicular ferrite is inhibited, the mass fraction of M-A island components is increased, the plasticity and toughness of steel are reduced, and the welding performance of steel is reduced. The invention controls the content of silicon in the range, and can improve the corrosion resistance and the mechanical property of the steel on the premise of not influencing the welding property.
The corrosion-resistant steel provided by the invention comprises 0.5-1.35% of Mn, more preferably 0.8-1.32%, and even more preferably 1.0-1.3% by mass. In the invention, the addition of manganese can make up for the strength loss caused by partial low carbon, and can also promote the nucleation capability of oxide on ferrite and promote the formation of ferrite. Manganese and sulfur form MnS with a high melting point, and the hot brittleness phenomenon caused by FeS formation can be prevented. In addition, manganese is also a good deoxidizer and desulfurizer, and is added together with silicon and titanium for composite deoxidation to form composite inclusion with higher sulfur capacity, thereby effectively inducing nucleation of acicular ferrite in the crystal. However, too high manganese content may cause manganese to form segregation zone in the steel, which is not favorable for improving the corrosion resistance of the steel. The invention controls the content of manganese in the range, and can improve the mechanical property of steel and the toughness of a welding heat affected zone on the basis of not affecting the corrosion resistance of the steel.
The corrosion-resistant steel provided by the invention comprises 0.1-0.4% of Cu by mass percentage, and preferably 0.2-0.3% of Cu by mass percentage. In the invention, copper element can be enriched in the rust layer to form a good protective rust layer; the stability of the rust layer is ensured by the firm bonding performance between the copper and the steel matrix, so that the corrosion resistance of the steel can be obviously improved; however, excessive amounts of copper lead to a reduction in the toughness of the weld heat affected zone and also to surface cracking of the steel during the manufacture of the steel. The invention controls the content of copper in the range, and can improve the corrosion resistance and the mechanical property of the steel on the premise of not influencing the welding property.
The corrosion-resistant steel provided by the invention comprises 0.1-0.5% of Ni, more preferably 0.2-0.4%, and even more preferably 0.25-0.3% of Ni in percentage by mass. In the invention, the nickel is a pure solid solution element in the steel, can strengthen a ferrite matrix and has the function of obviously reducing the ductile-brittle transformation temperature. In liquid or solid state, it can be mutually dissolved with Fe in any proportion, inhibit the formation of coarse pro-eutectoid ferrite, refine ferrite grains and improve the low-temperature toughness of steel. Meanwhile, nickel is an element for expanding an austenite phase region, can influence the diffusion speed of carbon and alloy elements, prevents pearlite from forming, improves hardenability, and slows down the quench hardening cracking tendency during welding. In addition, nickel element can be enriched in the rust layer, so that the contact between chloride ions and a matrix in a corrosive environment can be effectively prevented, and the corrosion resistance of the steel can be effectively improved. The invention controls the content of nickel in the range, and can improve the corrosion resistance of steel while improving the toughness of a welding heat affected zone.
The corrosion-resistant steel provided by the invention comprises 0.10-0.30% of Mo, more preferably 0.12-0.28%, and even more preferably 0.15-0.25% by mass. In the invention, the molybdenum can reduce an austenite phase region, effectively reduce the transformation temperature of bainite, and inhibit ferrite phase transformation, so that a complete bainite structure is obtained in a wider cooling speed range; the steel can be dissolved in ferrite, austenite and carbide in a solid state, and the stability of the carbide is improved, thereby improving the strength of the steel. The stable oxide of molybdenum or molybdate can be formed in the rust layer, so that the matrix is not easy to interact with chloride ions, the occurrence of pitting corrosion is inhibited, and the corrosion resistance of the steel is improved. The content of the molybdenum element is too high, so that the production cost is increased, excessive M-A components are easy to appear, and the toughness of a welding heat affected zone is reduced. According to the invention, the content of molybdenum is controlled within the range, so that the toughness of a welding heat affected zone is not influenced on the basis of improving the corrosion resistance of steel.
The corrosion-resistant steel provided by the invention comprises 0.01-0.05% of V, more preferably 0.02-0.04%, and even more preferably 0.25-0.30% in percentage by mass.
The corrosion-resistant steel provided by the invention comprises 0.005-0.035% of Ti, more preferably 0.01-0.03%, and even more preferably 0.015-0.025% by mass.
In the invention, vanadium, carbon, nitrogen and other elements have strong affinity, and vanadium-nitrogen compounds precipitated in austenite can inhibit austenite grains from growing. The vanadium-nitrogen compound separated out in the ferrite area can increase the nucleation core of ferrite in the crystal, and the two aspects act together to promote the grain refinement and obviously improve the welding performance of the steel. Titanium has strong affinity with oxygen, nitrogen and carbon, and is a good deoxidizer and an effective element for fixing nitrogen and carbon. The titanium oxide is effective in promoting acicular ferrite nucleation. Meanwhile, titanium can form fine and dispersed TiN particles in the steel, and can be slowly dissolved when the steel is heated to be more than 1400 ℃. In the welding process, tiN particles effectively prevent austenite grains from coarsening, and the toughness is improved; in addition, the TiN particles can effectively promote the formation of acicular ferrite and effectively improve the welding performance of the steel. Therefore, the contents of vanadium and titanium are controlled within the above ranges in consideration of the mechanical properties of steel and the high heat input weldability.
The corrosion-resistant steel provided by the invention comprises 0.01-0.06% of Sn in percentage by mass, more preferably 0.02-0.05%, and even more preferably 0.03-0.04%. According to the invention, the tin element is added, so that the enrichment can be realized in the rust layer, the compactness of the rust layer of the steel is improved, and meanwhile, a layer of protective film can be formed on the surface of the steel matrix, so that the self-corrosion potential of the steel in an acidic corrosion environment can be obviously improved, the corrosion resistance of the steel in the acidic corrosion environment can be effectively improved, but the tin element is easy to be segregated at a crystal boundary, and the mechanical property and the welding property of the steel can be seriously influenced due to overhigh content. The invention controls the content of tin within the range, and can not influence the mechanical property and the welding property of steel on the basis of improving the corrosion resistance.
The corrosion-resistant steel provided by the invention comprises, by mass, P not more than 0.012%, more preferably 0.005-0.011%, and even more preferably 0.006-0.010%.
The corrosion-resistant steel provided by the invention comprises, by mass, not more than 0.005% of S, more preferably 0.001-0.004%, and even more preferably 0.002-0.003%.
In the present invention, phosphorus and sulfur are inevitable as harmful impurity elements in steel, form segregation in steel, cause significant reduction in plasticity and toughness of steel, cause great damage to welding properties, and have adverse effects on corrosion resistance, and therefore, the present invention controls the contents of phosphorus and sulfur within the above-mentioned ranges.
The corrosion-resistant steel provided by the invention comprises 0.001-0.03% of Ce, more preferably 0.005-0.025%, and even more preferably 0.01-0.02% by mass.
The corrosion-resistant steel provided by the invention comprises, by mass, 0.001-0.03% of La, more preferably 0.005-0.025%, and even more preferably 0.01-0.02%.
In the invention, rare earth Ce and La are used as a deoxidizing agent and a desulfurizing agent to play roles in purification and tempering; meanwhile, ce and La can also react with oxides and sulfides in the steel to form fine spherical rare earth inclusions, so that pitting corrosion induced by the inclusions is reduced, and the corrosion resistance of the steel is improved; however, the high content of Ce and La elements results in a large amount of inclusions, and Ce and La elements are in solid solution and segregation at grain boundaries, which easily causes temper brittleness and at the same time has bad influence on corrosion resistance and welding performance. According to the invention, the content of Ce and La is controlled within the range, so that the corrosion resistance of the steel can be improved on the basis of not influencing the toughness of a welding heat affected zone.
The corrosion-resistant steel provided by the invention comprises 0.0002-0.005% of Ca, more preferably 0.0008-0.0048% of Ca, and even more preferably 0.0010-0.0045% of Ca in percentage by mass.
The corrosion-resistant steel provided by the invention comprises 0.0002-0.01% of Mg, more preferably 0.0005-0.0085%, and even more preferably 0.0008-0.008% by mass.
In the invention, the corrosion resistance of the steel can be improved by adding calcium and magnesium, and the calcium and magnesium are dissolved in water to form alkali in the corrosion process of the steel, so that the reduction of the pH value of the surface of the steel is inhibited, and the corrosion resistance of the steel is obviously improved. In addition, calcium and magnesium modify malignant sulfide inclusions in steel, which not only improves the weldability of steel but also further improves the local corrosion resistance.
The corrosion-resistant steel provided by the invention comprises 0.001-0.02% of Zr, more preferably 0.005-0.019%, and even more preferably 0.01-0.015% by mass. In the present invention, by adding Zr, sulfide can be formed in the steel by preferentially bonding with S, thereby reducing the generation of MnS and improving the pitting corrosion resistance of the steel. Trace amounts of Zr can produce the above effects. As the strong deoxidizing element, zr forms more oxide particles than Al and Ti, and is distributed more uniformly. However, excessive Zr can significantly reduce the toughness of the steel. Therefore, the invention controls the content of zirconium in the range, and can improve the corrosion resistance of steel without influencing the toughness of the steel.
The corrosion-resistant steel provided by the invention comprises, by mass, 0.005-0.3% of Co, more preferably 0.01-0.29%, and even more preferably 0.015-0.285%. According to the invention, a compact rust layer can be formed on the surface of the steel by adding cobalt, so that the expansion of local corrosion is inhibited, the corrosion resistance of the steel under the acid condition of a dry-wet alternative environment is improved, but the excessive cobalt can reduce the local corrosion resistance of the steel and influence the processing performance and the welding performance of the steel. The invention controls the cobalt content in the range, and can not influence the welding performance of the steel on the basis of improving the corrosion resistance of the steel.
The corrosion-resistant steel provided by the invention comprises, by mass, 0.0045-0.0065% of N, more preferably 0.005-0.006%, and even more preferably 0.0052-0.0058%. In the invention, a proper amount of nitrogen elements can form TiN, VN, BN and the like, can effectively refine crystal grains, improve the intragranular structure, induce the acicular ferrite to nucleate and can effectively improve the toughness of a welding heat affected zone.
The corrosion-resistant steel provided by the invention comprises, by mass, not more than 0.0030% of O.
In the invention, the mass percentage content of Ti, V, C and N is equal to or less than 0.04 and equal to or less than 2.35Ti +0.31V +0.02C +0.02N and equal to or less than 0.06.
In the invention, when the value of 2.35Ti +0.31V +0.02C +0.02N is more than 0.06, the size of precipitated particles in a welding heat affected zone formed by large heat input welding is increased, the austenite crystal boundary is pinned, and the effect of inhibiting the grain growth is weakened; when the value of 2.35Ti +0.31V +0.02C +0.02N is less than 0.04, the number of precipitated particles in the welding heat affected zone is reduced, the reduction of the number of acicular ferrite nucleation cores is promoted, and the improvement of the toughness of the welding heat affected zone is not facilitated.
The invention also provides a preparation method of the corrosion-resistant steel, which comprises the following steps:
heating, rough rolling, finish rolling, cooling and tempering the casting blank in sequence to obtain the corrosion-resistant steel;
the chemical components of the casting blank are consistent with those of the corrosion-resistant steel in the scheme.
In the present invention, the cast slab is preferably prepared; the preparation method preferably comprises the following steps:
smelting, refining and desulfurizing the raw materials in sequence to obtain refined molten steel and slag;
sequentially carrying out deoxidation treatment and alloying treatment on the refined molten steel to obtain alloyed molten steel;
and casting the alloyed molten steel to obtain the casting blank.
The smelting, refining and desulfurization processes are not particularly limited in the present invention, and may be performed by processes well known to those skilled in the art. In the present invention, the refining is preferably carried out in an LF refining furnace. The invention has no special limitation on the types and sources of raw materials for preparing the molten steel, and the raw materials are well known by the technical personnel in the field.
In the present invention, the slag floats on the surface of the refined molten steel. In the present invention, the basicity of the slag is preferably 5 to 7. In the present invention, when the basicity of the slag is not within the above range, it is preferable to adjust the basicity of the slag by adding quartz sand to the molten refining steel. The amount of the quartz sand added is not particularly limited in the present invention as long as the slag can be adjusted to a desired basicity.
After the refined molten steel and the slag are obtained, the invention separates the refined molten steel from the slag. The method of the present invention for the separation is not particularly limited, and may be carried out by a method known to those skilled in the art. In the present invention, the temperature of the molten refining steel is preferably not less than 1620 ℃.
After the refined molten steel is obtained, the invention carries out deoxidation treatment and alloying treatment on the refined molten steel in sequence to obtain alloyed molten steel.
In the present invention, the deoxidation raw material used in the deoxidation treatment is preferably ferrosilicon or aluminum wire. The process of the deoxidation treatment in the present invention is not particularly limited, and may be carried out by a process known to those skilled in the art. The amount of the deoxidizing raw material to be added in the present invention is not particularly limited, and those known to those skilled in the art may be used. In the present invention, the oxygen content in the molten steel obtained by the deoxidation treatment is preferably 30 to 60ppm, and more preferably 40 to 50ppm.
In the present invention, the raw material used for the alloying treatment is preferably a ferrotitanium alloy. The alloying treatment process of the present invention is not particularly limited, and may be performed by a process known to those skilled in the art. In the present invention, both the deoxidation treatment and the alloying treatment are preferably performed in a VD refining furnace; the vacuum degree of the VD refining furnace is preferably less than or equal to 5.0mbar, and the holding time is preferably more than or equal to 20min.
After the alloyed molten steel is obtained, the alloyed molten steel is cast to obtain the casting blank.
The casting process is not particularly limited in the present invention, and may be performed by a process known to those skilled in the art. In the invention, the thickness of the casting blank is preferably 260mm, and the width is preferably not less than 2570mm.
After the casting blank is obtained, the casting blank is heated. In the invention, the heating temperature is preferably 1190-1210 ℃, and more preferably 1195-1205 ℃; the time is preferably 9 to 16min/cm, more preferably 10 to 15min/cm, and still more preferably 11 to 13min/cm. In the present invention, a single-phase austenite structure can be obtained by heating, composition homogenization can be achieved, and deformation resistance can be reduced.
After the heating, the invention performs rough rolling on the heated casting blank. In the invention, the rolling temperature of the rough rolling is preferably 1050-1090 ℃, more preferably 1060-1080 ℃, and more preferably 1065-1070 ℃; the rough rolling is preferably multi-pass rolling, and is further preferably 5-7-pass rolling; the maximum reduction rate of the single pass is preferably equal to or more than 10%. In the present invention, the total reduction rate of the rough rolling is preferably not less than 50%. In the present invention, the thickness of the sheet obtained after the rough rolling is preferably 2.0 to 3.0 times the thickness of the cast slab.
After the rough rolling is finished, the invention also preferably comprises the step of carrying out first air cooling on the obtained plate. The first air cooling process is not particularly limited, and may be performed by a process known to those skilled in the art.
After the first air cooling is finished, the casting blank obtained after the first air cooling is subjected to finish rolling. In the present invention, the rolling temperature of the finish rolling is preferably 800 to 930 ℃, more preferably 820 to 910 ℃, and still more preferably 850 to 880 ℃; the initial rolling temperature of the finish rolling is preferably 900-930 ℃, and the final rolling temperature is preferably 810-840 ℃; the finish rolling is preferably multi-pass rolling, and more preferably 5 to 7-pass rolling; the maximum reduction rate per pass is preferably not less than 10%. In the present invention, the total reduction rate of the finish rolling is preferably not less than 50%.
After the finish rolling is finished, the casting blank obtained by the finish rolling is cooled. In the invention, the cooling starting temperature is preferably 760-800 ℃, more preferably 770-790 ℃, and more preferably 775-780 ℃; the cooling rate is preferably not less than 6 ℃/s, more preferably 12 to 15 ℃/s, and still more preferably 13 to 14 ℃/s. In the present invention, the cooling preferably includes performing water cooling and second air cooling in this order. The processes of the water cooling and the second air cooling are not particularly limited in the present invention, and may be performed by processes well known to those skilled in the art.
In the present invention, the temperature of the returning red of the cast slab obtained after the water cooling is preferably 530 to 570 ℃, more preferably 540 to 560 ℃, and still more preferably 545 to 550 ℃.
In the present invention, it is preferable that the temperature of the cast slab is lowered to room temperature by the second air cooling.
In the present invention, the tempering temperature is preferably 500 to 650 ℃, and more preferably 600 to 650 ℃. In the present invention, the tempering time is calculated according to the following formula:
t (tempering time/min) = 2-2.5 (heating coefficient/min mm) -1 ) XD (steel plate thickness/mm) +10 to 20 (additional time/min).
In the present invention, the thickness of the corrosion-resistant steel is preferably 18 to 40mm.
The invention also provides application of the corrosion-resistant steel in the technical scheme or the corrosion-resistant steel prepared by the preparation method in the technical scheme in a crude oil storage tank.
The invention also provides a crude oil storage tank which is prepared by welding steel serving as a raw material, wherein the steel is the corrosion-resistant steel in the technical scheme or the corrosion-resistant steel prepared by the preparation method in the technical scheme.
In the present invention, the welding is preferably a high heat input welding; the heat input of the weld is preferably 50 to 100kJ/cm.
In the present invention, the weld-formed weld joint preferably includes a weld bead region, a fusion region, and a weld heat affected zone.
In the present invention, the number density of (V, ti) (C, N) composite precipitated particles among the precipitated particles having a size of 20 to 80nm in the welding heat affected zone is preferably (1.83 to 3.36). Times.10 5 Per mm 3 (ii) a The number of the (V, ti) (C, N) composite precipitated particles is preferably 60 to 70% of the total number of particles. In the present invention, the precipitated particles having a size of 20 to 80nm can suppress the growth of austenite grains.
In the present invention, among the precipitated particles having a size of 0.5 to 1.5 μm in the welding heat affected zone, (Ti, V) (C, N) composite precipitated particles have a value of (2.88 to 5.12). Times.10 4 Per mm 3 (ii) a The number of the (Ti, V) (C, N) composite precipitated particles is preferably 60 to 70% of the total number of particles. In the present invention, the precipitated particles having a size of 0.5 to 1.5 μm can be heteronucleated.
For further explanation of the present invention, the corrosion-resistant steel, the preparation method and the application thereof, and the crude oil storage tank according to the present invention will be described in detail with reference to the accompanying drawings and examples, which should not be construed as limiting the scope of the present invention.
Examples 1 to 5
Smelting, refining and desulfurizing the molten steel in sequence to obtain refined molten steel and slag; the refining is carried out in an LF refining furnace; the temperature of the refining molten steel is 1650 ℃; the basicity of the slag is 6;
introducing the refining molten steel into a VD refining furnace, and deoxidizing by adopting an aluminum wire to obtain molten steel with the oxygen content of 45ppm; then adding ferrotitanium alloy for alloying treatment to obtain alloyed molten steel; the vacuum degree of the VD refining furnace is 5.0mbar, and the holding time is 25min;
casting the alloyed molten steel to obtain a casting blank (the thickness is 260mm, and the width is 2570 mm);
sequentially heating, rough rolling, finish rolling, cooling and tempering the obtained casting blank to obtain the corrosion-resistant steel (the thickness is 21.5 mm); the compositions of the corrosion-resistant steel are shown in table 1; wherein, the results obtained by calculating the total mass percentage of Ti, V, C and N according to 2.35Ti +0.31V +0.02C +0.02N (regulation and control formula) are shown in Table 2;
the condition parameters of the heating, rough rolling, finish rolling, cooling and tempering treatments are shown in Table 3.
Comparative examples 1 to 3
Smelting, refining and desulfurizing the molten steel in sequence to obtain refined molten steel and slag; the refining is carried out in an LF refining furnace; the temperature of the refining molten steel is 1650 ℃; the alkalinity of the slag is 5-7;
introducing the refining molten steel into a VD refining furnace, and deoxidizing by adopting ferrosilicon or aluminum wires to obtain molten steel with the oxygen content of 45ppm; then adding ferrotitanium alloy for alloying treatment to obtain alloyed molten steel; the vacuum degree of the VD refining furnace is 5.0mbar, and the holding time is 25min;
casting the alloyed molten steel to obtain a casting blank (the thickness is 260mm, and the width is 2570 mm);
sequentially heating, rough rolling, finish rolling, cooling and tempering the obtained casting blank to obtain the corrosion-resistant steel (with the thickness of 21.5 mm); the compositions of the corrosion-resistant steel are shown in table 1; wherein, the results obtained by calculating the total mass percentage of Ti, V, C and N according to 2.35Ti +0.31V +0.02C +0.02N (regulation and control formula) are shown in Table 2;
the condition parameters of the heating, rough rolling, finish rolling, cooling and tempering treatments are shown in Table 3.
TABLE 1 compositions of corrosion-resistant steels obtained in examples 1 to 5 and comparative examples 1 to 3
TABLE 2 results of calculation of regulation formula in examples 1 to 5 and comparative examples 1 to 3
| Regulating and controlling type | 2.35Ti+0.31V+0.02C+0.02N |
| Standard range of | 0.04～0.06 |
| Example 1 | 0.044 |
| Example 2 | 0.058 |
| Example 3 | 0.048 |
| Example 4 | 0.055 |
| Example 5 | 0.057 |
| Comparative example 1 | 0.082 |
| Comparative example 2 | 0.10 |
| Comparative example 3 | 0.063 |
TABLE 3 Condition parameters in examples 1 to 5 and comparative examples 1 to 3
Performance test
Test example 1
The corrosion-resistant steels obtained in the examples 1 to 5 and the comparative examples 1 to 3 are processed into Gleeble thermal simulation samples with the thickness of 10.5mm multiplied by 80mm, and a welding thermal simulation experiment with the heat input of 85kJ/cm is carried out on a Gleeble-3500 thermal simulation testing machine, and the experimental steps are as follows: heating the sample to 1350 ℃ at the heating rate of 100 ℃/s, staying for 1s, setting the thickness of the simulated plate to be 32mm, and setting the heat input to be 85kJ/cm; then processing the sample into a standard impact sample with the diameter of 10mm multiplied by 55mm, carrying out an impact test under the condition of-20 ℃, and obtaining the test results as shown in table 4;
TABLE 4 results of low-temperature impact property test of heat-affected zone formed after weld heat simulation test for corrosion resistance obtained in examples 1 to 5 and comparative examples 1 to 3
As can be seen from Table 4, after the corrosion-resistant steel obtained by the invention is subjected to heat input of 85kJ/cm, the impact energy of a coarse grain heat affected zone at the temperature of-20 ℃ is averagely more than 100J, and the low-temperature toughness is excellent.
Metallographic microscope is adopted to detect metallographic structures of the coarse-grained heat affected zone formed after the corrosion resistance of the working example 4 and the working example 1 are subjected to the welding heat simulation experiment, and the obtained metallographic structure diagrams are shown in fig. 1 and fig. 2, wherein fig. 1 is the metallographic structure diagram of the coarse-grained heat affected zone in the working example 4, and fig. 2 is the metallographic structure diagram of the coarse-grained heat affected zone in the working example 1; it can be seen from fig. 1 and 2 that the grain size of the example is smaller and the acicular ferrite is more, the grain size of the comparative example is larger, and the coarser grains in the coarse grain heat affected zone make the crack more easily propagate in the impact test and the toughness is poorer. Therefore, the toughness of a coarse grain heat affected zone formed by the corrosion-resistant steel obtained by the embodiment of the invention after being welded by large heat input is better, and the corrosion-resistant steel provided by the invention has good welding performance.
Test example 2
The corrosion-resistant steels obtained in examples 1 to 5 and comparative examples 1 to 3 were subjected to a mechanical property test;
testing according to the national standard GB/T1591-2008 'Low alloy high strength structural Steel' for Q235B steel for a common bottom plate of a petroleum storage tank;
the test results obtained are shown in table 5;
TABLE 5 mechanical Properties of Corrosion-resistant steels obtained in examples 1 to 5 and comparative examples 1 to 3
As can be seen from Table 5, the corrosion-resistant steel provided by the invention has better mechanical properties, the yield strength is more than 360MPa, the tensile strength is more than 510MPa, the elongation is more than 20%, and the impact energy at-20 ℃ is more than 120J.
Test example 3
The corrosion-resistant steels obtained in examples 1 to 5 and comparative examples 1 to 3 were processed and sampled to obtain rectangular corrosion coupons having dimensions of 25mm × 60mm × 5mm, which were placed in an experimental apparatus (wherein 1 water bath heating device, 2 beaker, 3 immersion corrosion solution, 4 immersion corrosion test coupon sample, and 5 water) as shown in fig. 3, and the experiment was performed by water bath heating, and the immersion solution was acidic Cl having a pH of 0.85 - The solution etching period is 72h, and the solution is replaced every 24 h. The experiment is carried out according to IMO standard of inspection guidelines for corrosion-resistant steel materials of cargo oil tanks of crude oil tanker to simulate the corrosion of the inner bottom of steel of a crude oil storage tank. After the experiment is finished, carrying out rust removal treatment on the samples, calculating the corrosion weight loss of each sample, and calculating the corrosion rate; the results obtained are shown in table 6;
wherein, the real object diagrams after the corrosion of the example 1 and the comparative example 1 are shown in FIG. 4;
TABLE 6 Corrosion Rate of Corrosion-resistant steels obtained in examples 1 to 5 and comparative examples 1 to 3
As can be seen from table 6 and fig. 4, the corrosion-resistant steel provided by the present invention has excellent corrosion resistance.
In conclusion, the corrosion-resistant steel provided by the invention has excellent corrosion resistance and good large heat input resistance; under the condition of large heat input, the coarse-grain heat affected zone still has higher toughness, can be suitable for the wallboard structure of a large crude oil storage tank, the anti-corrosion structure of ocean and ship and the like, and has the advantages of capability of improving the construction efficiency by times, low energy consumption, good economic benefit, capability of industrial mass production and the like.
Although the above embodiments have been described in detail, they are only a part of the embodiments of the present invention, not all of the embodiments, and other embodiments can be obtained without inventive step according to the embodiments, and all of the embodiments belong to the protection scope of the present invention.
Claims (10)
1. The corrosion-resistant steel is characterized by comprising the following components in percentage by mass: c:0.03 to 0.07%, si: 0.06-0.25%, mn: 0.5-1.35%, P is less than or equal to 0.012%, S is less than or equal to 0.005%, cu:0.1 to 0.4%, ni: 0.1-0.5%%, mo:0.10 to 0.30%, V:0.01 to 0.05%, ti: 0.005-0.035%, sn:0.01 to 0.06 percent, ce:0.001 to 0.03%, la:0.001 to 0.03%, ca:0.0002 to 0.005%, mg:0.0002 to 0.001%, zr:0.001 to 0.02%, co: 0.005-0.3%, O is less than or equal to 0.0030%, N:0.0045 to 0.0065 percent of the total weight of the alloy, and the balance of Fe and inevitable impurities;
wherein, the mass percentage content of Ti, V, C and N satisfies 0.04 ≤ 2.35Ti +0.31V +0.02C +0.02N ≤ 0.06.
2. The method of producing corrosion-resistant steel according to claim 1, characterized by comprising the steps of:
heating, rough rolling, finish rolling, cooling and tempering the casting blank in sequence to obtain the corrosion-resistant steel;
the chemical composition of the casting blank is consistent with the chemical element composition of the corrosion-resistant steel of claim 1.
3. The method according to claim 2, wherein the heating temperature is 1190 to 1210 ℃ and the holding time is 9 to 16min/cm.
4. The production method according to claim 2, wherein the rolling temperature of the rough rolling is 1050 to 1090 ℃;
the rough rolling is multi-pass rolling, and the maximum reduction rate of a single pass is more than or equal to 10%.
5. The production method according to claim 2, wherein the finish rolling is performed at a rolling temperature of 800 to 930 ℃;
the initial rolling temperature of the finish rolling is 900-930 ℃, and the final rolling temperature is 810-840 ℃;
the finish rolling is multi-pass rolling, and the maximum reduction rate of a single pass is more than or equal to 10%.
6. The preparation method according to claim 2, wherein the cooling start-cooling temperature is 760-800 ℃, and the cooling rate is not less than 6 ℃/s;
the temperature of the return red of the casting blank obtained after cooling is 530-570 ℃.
7. The method of claim 2, wherein the tempering temperature is 500 to 650 ℃.
8. Use of the corrosion-resistant steel of claim 1 or the corrosion-resistant steel prepared by the preparation method of any one of claims 2 to 7 in a crude oil storage tank.
9. A crude oil storage tank, which is prepared by welding steel materials as raw materials, and is characterized in that the steel materials are the corrosion-resistant steel according to claim 1 or the corrosion-resistant steel prepared by the preparation method according to any one of claims 2 to 7.
10. The crude oil storage tank of claim 9, wherein the weld is a high heat input weld;
the weld-formed weld joint comprises a weld joint region, a fusion region, and a weld heat affected zone;
the number of (V, ti) (C, N) composite precipitated particles in the precipitated particles with the size of 20-80 nm in the welding heat affected zone accounts for 60-70%;
the number of (Ti, V) (C, N) composite precipitated particles in the weld heat affected zone is 60-70% of precipitated particles having a size of 0.5-1.5 [ mu ] m.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211225169.8A CN115948693A (en) | 2022-10-09 | 2022-10-09 | Corrosion-resistant steel, preparation method and application thereof, and crude oil storage tank |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211225169.8A CN115948693A (en) | 2022-10-09 | 2022-10-09 | Corrosion-resistant steel, preparation method and application thereof, and crude oil storage tank |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN115948693A true CN115948693A (en) | 2023-04-11 |
Family
ID=87290169
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202211225169.8A Pending CN115948693A (en) | 2022-10-09 | 2022-10-09 | Corrosion-resistant steel, preparation method and application thereof, and crude oil storage tank |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115948693A (en) |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102492896A (en) * | 2011-12-29 | 2012-06-13 | 钢铁研究总院 | Steel for upper deck of cargo oil tank of tanker |
| CN105420596A (en) * | 2015-11-24 | 2016-03-23 | 钢铁研究总院 | Corrosion-resistant steel for crude oil storage and transportation container and preparation method of corrosion-resistant steel |
| WO2022054866A1 (en) * | 2020-09-10 | 2022-03-17 | 日本製鉄株式会社 | Steel sheet and method for producing same |
-
2022
- 2022-10-09 CN CN202211225169.8A patent/CN115948693A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102492896A (en) * | 2011-12-29 | 2012-06-13 | 钢铁研究总院 | Steel for upper deck of cargo oil tank of tanker |
| CN105420596A (en) * | 2015-11-24 | 2016-03-23 | 钢铁研究总院 | Corrosion-resistant steel for crude oil storage and transportation container and preparation method of corrosion-resistant steel |
| WO2022054866A1 (en) * | 2020-09-10 | 2022-03-17 | 日本製鉄株式会社 | Steel sheet and method for producing same |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109082591B (en) | 125ksi hydrogen sulfide stress corrosion resistant high-strength oil casing steel and preparation process thereof | |
| CN114959460B (en) | Low-yield-ratio easy-welding weather-resistant bridge steel and manufacturing method thereof | |
| CN112080702B (en) | Weather-resistant bridge steel with impact absorption power of not less than 60J at-60 ℃ in welded coarse grain heat affected zone | |
| CN115725899B (en) | Corrosion-resistant steel, preparation method and application thereof, and crude oil storage tank | |
| JP2011202214A (en) | Thick high tensile strength steel plate having excellent low temperature toughness in multilayer weld zone and method for producing the same | |
| CN114134407A (en) | Easy-to-weld steel plate with excellent low-temperature toughness at core for volute and manufacturing method thereof | |
| CN108342649B (en) | Acid corrosion resistant quenched and tempered high-strength steel for pressure vessel and production method thereof | |
| KR20230172017A (en) | Corrosion-resistant high-strength steel plate for marine engineering capable of high heat input welding and method of manufacturing the same | |
| CN113046635A (en) | High-strength and high-toughness corrosion-resistant steel for ocean engineering and manufacturing method thereof | |
| CN114959468B (en) | Nickel-free L360MSX52MS H-resistant thick-specification extreme cold-resistant 2 S-corrosion hot-rolled coil and preparation method thereof | |
| CN113832413B (en) | Ultra-thick 800 MPa-grade quenched and tempered steel plate with excellent core low-temperature impact toughness and weldability and manufacturing method thereof | |
| US10837089B2 (en) | Thick steel plate for high heat input welding and having great heat-affected area toughness and manufacturing method therefor | |
| CN115717214B (en) | Steel for coastal atmospheric environment refining pipeline and preparation method thereof | |
| CN111893401A (en) | L450MS pipeline steel with excellent SSCC resistance under high loading stress and manufacturing method thereof | |
| JPH05271766A (en) | Manufacture of high strength steel plate excellent in hydrogen induced cracking resistance | |
| CN114908292B (en) | Steel plate for evaporator of advanced nuclear power unit and manufacturing method thereof | |
| KR20210080698A (en) | Fitting part having excellent resistance to hydrogen induced cracking and manufacturing method for the same | |
| JP5008879B2 (en) | High strength steel plate with excellent strength and low temperature toughness and method for producing high strength steel plate | |
| CN114381652B (en) | Corrosion-resistant steel and steel plate for low-density mobile pressure container and manufacturing method thereof | |
| CN114959459A (en) | Steel plate for advanced nuclear power unit reactor core shell barrel and manufacturing method thereof | |
| CN115948693A (en) | Corrosion-resistant steel, preparation method and application thereof, and crude oil storage tank | |
| JP4144121B2 (en) | Non-tempered high strength steel with excellent toughness of base metal and weld heat affected zone | |
| JP3854412B2 (en) | Sour-resistant steel plate with excellent weld heat-affected zone toughness and its manufacturing method | |
| CN113832387A (en) | Low-cost ultra-thick 1000 MPa-grade steel plate and manufacturing method thereof | |
| JP2705946B2 (en) | Manufacturing method of high strength steel sheet with excellent SSC resistance |
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 |