CN104498836B - A kind of corrosion-proof rare earth steel alloy - Google Patents
A kind of corrosion-proof rare earth steel alloy Download PDFInfo
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Abstract
The invention discloses a kind of corrosion-proof rare earth steel alloy, relate to rare earth alloy steel field, by mass percentage, this rare earth alloy steel includes the C of 0%��0.10%, the Si of 0.20%��0.50%, the Mn of 0.40%��0.60%, the P of 0%��0.018%, the S of 0%��0.005%, the Cr of 1.8%��2.0%, the Ni of 0%��0.3%, the Mo of 0.30%��0.50%, the Al of 0.04%��0.08%, the V of 0.08%��0.12%, the Nb of 0.04%��0.08%, the Cu of 0%��0.20%, the rare earth of 0.005%��0.03%, surplus is Fe, rare earth includes the La of 20%��40%, the Ce of 40%��50%, the Pr of Nd and 1% of 15%��20%��5%. the rare earth alloy steel of the present invention, under the premise with good obdurability, heat-resisting quantity, welding performance, improves the anti-H 2 S stress corrosion ability of steel, resistant to hydrogen causes ability and the anti-chlorine ion corrosion ability of induced cracking, and use cost is relatively low.
Description
Technical field
The present invention relates to rare earth alloy steel field, be specifically related to a kind of corrosion-proof rare earth steel alloy.
Background technology
There is Wet H2S environment (H in the Pressure vessels in existing petrochemical industry2And chloride ion (Cl S)-) corrosive conditions, therefore, petrochemical equipment needs to adopt corrosion resistant steel to make, the carbon steel that traditional petrochemical equipment corrosion resisting steel generally adopts the trade mark to be Q345R (HIC), Q245R (HIC) or SA516Gr.70 (HIC) is made, and the alloy content of carbon steel is relatively low, and intensity is relatively low, under high-temperature and high-pressure conditions easily impaired, Steel for Petrochemicai Equipment after impaired is difficult to reuse, it is necessary to be replaced, and use cost is higher.
Therefore, existing Steel for Petrochemicai Equipment is 12Cr2Mo1R at the usual employing trade mark in hydrogen environment that faces of middle high temperature, 12Cr2Mo1VR, or the hydrogen steel plate that faces of 15CrMoR (H) is made, this faces hydrogen steel plate in use, the High Temperature High Pressure in equipment use procedure can be born, but it is in the hydrogen sulfide of humidity and the environment of chloride ion for a long time, hydrogen sulfide and chloride ion can be mutually promoted and be aggravated corrosion, cause facing hydrogen steel plate generation sulphide stress corrosion and chloride ion stress corrosion, hydrogen steel plate intensity of facing after corrosion reduces, in equipment use procedure, the hydrogen steel plate that faces after corrosion is susceptible to breakage, it is difficult to be continuing with.
The patent of invention that the patent No. is CN102925814A discloses " a kind of anti-H 2 S stress corrosion steels for pressure vessel use and production method thereof ", by controlling S, P content in steel, steel are made to have good resistance against hydrogen cracking and anti-H 2 S stress corrosion performance, but the tensile strength of this steel plate is relatively low, heat resistance is not strong, is not suitable for the petrochemical equipment of middle hot environment, and when for high pressure petrochemical equipment, needing the steel plate using thickness bigger, use cost is higher.
The application for a patent for invention that the patent No. is CN102605242A discloses " a kind of resistance against hydrogen cracking steels for pressure vessel use and manufacture method thereof " by the C content in increase steel to 0.15%��0.25%, increases the intensity of steel;But being as the increase of phosphorus content, steel are not only susceptible to hydrogen attack, and solderability is poor, therefore, these steel are difficult to use in the pressure vessel preparing petrochemical equipment.
Summary of the invention
For the defect existed in prior art, it is an object of the invention to provide a kind of corrosion-proof rare earth steel alloy, under the premise with good obdurability, heat-resisting quantity, welding performance, the raising anti-H 2 S stress corrosion ability of steel, resistant to hydrogen cause ability and the anti-chlorine ion corrosion ability of induced cracking, and use cost is relatively low.
For reaching object above, the present invention adopts the technical scheme that: a kind of corrosion-proof rare earth steel alloy, by mass percentage, this rare earth alloy steel includes the C of 0%��0.10%, the Si of 0.20%��0.50%, the Mn of 0.40%��0.60%, the P of 0%��0.018%, the S of 0%��0.005%, the Cr of 1.8%��2.0%, the Ni of 0%��0.3%, the Mo of 0.30%��0.50%, the Al of 0.04%��0.08%, the V of 0.08%��0.12%, the Nb of 0.04%��0.08%, the Cu of 0%��0.20%, the rare earth of 0.005%��0.03%, surplus is Fe, rare earth includes the La of 20%��40%, the Ce of 40%��50%, the Pr of Nd and 1% of 15%��20%��5%.
On the basis of technique scheme, by mass parts, described rare earth alloy steel includes the C of 0%��0.08%, the Si of 0.25%��0.45%, the Mn of 0.42%��0.55%, the P of 0%��0.014%, the S of 0%��0.0035%, the Cr of 1.82%��1.98%, the Ni of 0%��0.2%, the Mo of 0.32%��0.48%, the Al of 0.05%��0.07%, the V of 0.09%��0.11%, the Nb of 0.05%��0.07%, the Cu of 0%��0.15%, the rare earth of 0.007%��0.020%, surplus is Fe, rare earth includes the La of 20%��40%, the Ce of 40%��50%, the Pr of Nd and 1% of 15%��20%��5%.
On the basis of technique scheme, by mass parts, described rare earth alloy steel includes the C of 0%��0.05%, the Si of 0.30%��0.40%, the Mn of 0.45%��0.52%, the P of 0%��0.012%, the S of 0%��0.003%, the Cr of 1.85%��1.95%, the Ni of 0%��0.15%, the Mo of 0.35%��0.45%, the Al of 0.055%��0.65%, the V of 0.095%��0.105%, the Nb of 0.055%��0.065%, the Cu of 0%��0.10%, the rare earth of 0.008%��0.015%, surplus is Fe, rare earth includes the La of 20%��40%, the Ce of 40%��50%, the Pr of Nd and 1% of 15%��20%��5%.
On the basis of technique scheme, the content of described rare earth alloy steel middle rare earth is 0.01%.
On the basis of technique scheme, described rare earth include 30% La, 48% Ce, 19% the Pr of Nd and 3%.
On the basis of technique scheme, the yield strength of described rare earth alloy steel is 380��390MPa, and tensile strength is 540��565MPa.
On the basis of technique scheme, the contraction percentage of area of described rare earth alloy steel is 63%��65%, and elongation after fracture is 31%��32%, and percentage elongation is 34.5%.
On the basis of technique scheme, described grain size is more than 6 grades, and the summation of nonmetallic inclusion is less than 4.0.
On the basis of technique scheme, described rare earth alloy steel ballistic work at 0 DEG C is 228J, ballistic work at-30 DEG C is 205J.
A kind of method preparing corrosion-proof rare earth steel alloy, comprises the following steps:
A, raw material is put in electric furnace refine, obtain molten steel;Molten steel is transferred to external refining bag and carries out external refining and vacuum outgas, adjust the content of C in ladle be 0%��0.10%, the content of Si be 0.20%��0.50%, the content of Mn be 0.40%��0.60%, the content 0%��0.018% of P, the content 0%��0.005% of S, the content of Cr is 1.8%��2.0%, the content 0%��0.3% of Ni, the content of Mo is 0.30%��0.50%, the content of Al is 0.04��0.08%, the content of V is 0.08��0.12%, the content of Nb is 0.04��0.08%, the content 0%��0.2% of Cu;
The casting molding of B, bull ladle obtains electrode billet, electrode billet is carried out electroslag remelting, obtain rare earth alloy steel electroslag ingot, nearly finished product is obtained by after electroslag ingot hot-working, roughing, nearly finished product is carry out 700 �� 10 DEG C of temper after 950 �� 10 DEG C of normalized treatment through temperature, obtains rare earth alloy steel finished product then through polish.
Compared with prior art, it is an advantage of the current invention that:
(1) rare earth alloy steel in the present invention, its yield strength is 380��390MPa, tensile strength is 540��565MPa, the contraction percentage of area is 63��65%, elongation after fracture is 31��32%, and grain size is more than 6 grades, and the summation of nonmetallic inclusion is less than 4.0, ballistic work at 0 DEG C is 228J, ballistic work at-30 DEG C is 205J, and the percentage elongation of this steel alloy is 34.5%. The rare earth alloy steel of the present invention, compared with steel of the prior art, its comprehensive comparison is superior, not easily impaired at high temperature under high pressure, it is possible to be used for preparing Steel for Petrochemicai Equipment. Meanwhile, when Steel for Petrochemicai Equipment prepared by this rare earth alloy steel, not only solderability is higher, and the thinner thickness of the rare earth alloy steel needed, it is possible to save cost.
(2) rare earth alloy steel in the present invention, its resistance to sulphuric acid, ferric chloride, hydrochloric acid, the homogeneous corrosion ability of hydrogen sulfide is stronger, owing to the comparison of ingredients of oil and industrial chemicals is complicated, usually contain sulfide, hydrogen, Wet H2S environment and chloride ion, if Steel for Petrochemicai Equipment is corroded by any of which composition, device damage can be caused, therefore, need to select the steel being prevented from the corrosion of any one composition to prepare Steel for Petrochemicai Equipment, rare earth alloy steel in the present invention disclosure satisfy that above-mentioned requirements, therefore, rare earth alloy steel can be used in preparation can the Steel for Petrochemicai Equipment of life-time service, extend the service life of Steel for Petrochemicai Equipment, reduce the use cost of Steel for Petrochemicai Equipment.
(3) rare earth alloy steel in the present invention, through normalizing at the temperature of 950 �� 10 DEG C, obtain after tempering at the temperature of 700 �� 10 DEG C, this rare earth alloy steel is organized as stable ferrite+sorbite tissue, it is absent from the martensitic structure that hydrogen sulfide splitting and hydrogen induced cracking (HIC) are had considerable influence, and then increases the anti-H 2 S stress corrosion ability of rare earth alloy steel.
Accompanying drawing explanation
Fig. 1 is the metallograph of corrosion-proof rare earth steel alloy in the embodiment of the present invention.
Detailed description of the invention
Below in conjunction with drawings and Examples, the present invention is described in further detail.
Shown in Figure 1, the embodiment of the present invention provides a kind of corrosion-proof rare earth steel alloy, by mass percentage, this rare earth alloy steel includes the C (carbon) of 0%��0.10%, the Si (silicon) of 0.20%��0.50%, the Mn (manganese) of 0.40%��0.60%, the P (phosphorus) of 0%��0.018%, the S (sulfur) of 0%��0.005%, the Cr (chromium) of 1.8%��2.0%, the Ni (nickel) of 0%��0.3%, the Mo (molybdenum) of 0.30%��0.50%, the Al (aluminum) of 0.04%��0.08%, the V (vanadium) of 0.08%��0.12%, the Nb (niobium) of 0.04%��0.08%, the Cu (copper) of 0%��0.20%, the rare earth of 0.005%��0.03% is (in the present embodiment, the content of rare earth is preferably 0.01%), surplus is Fe (ferrum) and inevitable impurity.
In the embodiment of the present invention, by mass parts, corrosion-proof rare earth steel alloy includes the C of 0%��0.08%, the Si of 0.25%��0.45%, the Mn of 0.42%��0.55%, the P of 0%��0.014%, the S of 0%��0.0035%, the Cr of 1.82%��1.98%, the Ni of 0%��0.2%, the Mo of 0.32%��0.48%, the Al of 0.05%��0.07%, the V of 0.09%��0.11%, the Nb of 0.05%��0.07%, the Cu of 0%��0.15%, the rare earth of 0.007%��0.020%, surplus is Fe and inevitable impurity.
In the embodiment of the present invention, by mass parts, corrosion-proof rare earth steel alloy includes the C of 0%��0.05%, the Si of 0.30%��0.40%, the Mn of 0.45%��0.52%, the P of 0%��0.012%, the S of 0%��0.003%, the Cr of 1.85%��1.95%, the Ni of 0%��0.15%, the Mo of 0.35%��0.45%, the Al of 0.055%��0.65%, the V of 0.095%��0.105%, the Nb of 0.055%��0.065%, the Cu of 0%��0.10%, the rare earth of 0.008%��0.015%, surplus is Fe and inevitable impurity.
20%��40%La (lanthanum) that rare earth in the embodiment of the present invention includes, the Ce (cerium) of 40%��50%, 15%��20% the Pr (praseodymium) of Nd (neodymium) and 1%��5%.
In the embodiment of the present invention, rare earth include 30% La, 48% Ce, 19% the Pr of Nd and 3%.
The preparation method of embodiment of the present invention middle rare earth steel alloy is as follows:
S1: adding Fe in electric furnace with eccentric bottom, the Al being initially charged mass parts 0%��0.01% during tapping carries out preliminary deoxidation, is subsequently adding Si, Mn, Cr, Mo, Ni, V, Nb element and carries out preliminary alloying, obtains molten steel.
S2: molten steel is transferred to external refining bag and carries out LF external refining and vacuum outgas, adding aluminum in degassed backward steel is 0.05%��0.08% to the content of aluminum in steel, add rare earth and keep little argon stirring more than 15min, adjusting the content of C in ladle is 0%��0.10%, the content of Si is 0.20%��0.50%, the content of Mn is 0.40%��0.60%, the content 0%��0.018% of P, the content 0%��0.005% of S, the content of Cr is 1.8%��2.0%, the content 0%��0.3% of Ni, the content of Mo is 0.30%��0.50%, the content of Al is 0.04��0.08%, the content of V is 0.08��0.12%, the content of Nb is 0.04��0.08%, the content 0%��0.2% of Cu.
S3: bull ladle casting molding obtains electrode billet, electrode billet is carried out electroslag remelting, obtain rare earth alloy steel electroslag ingot, nearly finished product is obtained by after electroslag ingot hot-working, roughing, nearly finished product is carry out 700 �� 10 DEG C of temper after 950 �� 10 DEG C of normalized treatment through temperature, obtains rare earth alloy steel finished product then through polish.
Shown in Figure 1, rare earth alloy steel finished product be organized as stable ferrite+sorbite tissue, in figure, white is ferritic structure, it is absent from the martensitic structure that hydrogen sulfide splitting and hydrogen induced cracking (HIC) are had considerable influence, and then increases the anti-H 2 S stress corrosion ability of rare earth alloy steel finished product.
Adopting the rare earth alloy steel that said method prepares, its tensile strength is 540��565MPa, and yield strength is 380��390MPa, the contraction percentage of area is 63%��65%, elongation after fracture is 31%��32%, and grain size is more than 6 grades, and the summation of nonmetallic inclusion is less than 4.0.
In embodiment of the present invention medium alloy steel, the content of carbon is 0%��0.10%, when being 0.08%��0.25% due to carbon content, the halophile corrosivity of steel alloy is higher, if after carbon content is higher than 0.25%, along with the increase of carbon content in steel alloy, steel alloy is not only susceptible to hydrogen attack, and solderability is poor, the carbon content of embodiment of the present invention medium alloy steel is for controlling below 0.10%, and this steel alloy can not only corrode by halophile, and solderability is better.
In the embodiment of the present invention, the content of Mn is 0.40%��0.60%, owing to manganese element is the element of a kind of easy segregation, controlling Fe content is the effective way avoiding steel alloy to ftracture at sulfide corrosion, when the Mn of line of segragation, C content reach certain proportion, produce and in equipment welding process at steel, it is easy to produce martensitic phase. The hardness of martensitic phase is higher, can reduce the ability of equipment resisting sulfide stress corrosion; Meanwhile, when in steel alloy, the content of manganese is 0.40%��0.60%, manganese can produce Manganese monosulfide. with the reaction of Salmon-Saxl in steel alloy, discharges steel alloy system. Meanwhile, steel alloy is when deoxidation, and content is the manganese of 0.40%��0.60%, it is possible to form good deoxidation tissue, promotes steel alloy deoxidation, and has a positive effect.
In the embodiment of the present invention, the content of Cr is 1.8%��2.0%, the fusing point of Cr is 1903 DEG C, itself there is good creep-resistant property, when in steel alloy, the content of Cr is 1.8%��2.0%, this steel alloy has good creep-resistant property, when in steel alloy the content of Cr lower than 1.8% or higher than 2.0% time, its creep-resistant property is below the steel alloy that Cr content is 1.8%��2.0%.
Chromium, aluminum, silicon and rare earth element can improve the antioxygenic property of heat resisting steel.
In the embodiment of the present invention, the content of Mo is 0.30%��0.50%, the fusing point of Mo is 2625 DEG C, it it is a kind of refractory metal, after Mo adds steel alloy, ��-Fe phase region can be reduced, expand the alloying element various configuration of ferrum elemental crystal (��-Fe, the ��-Fe are) of ��-Fe phase region, resistant to hydrogen ability and the heat resistance of anti-H 2 S cracking performance, raising heat resisting steel can be improved, significantly inhibit the self-diffusion of ferrum, improve the recrystallization temperature of solid solution. In the content relatively Mayari of Mo, the effect of Mo is Intensive intervention part and the tiny Carbide Phases forming excellent. The anti-H 2 S cracking effect of Mo is equivalent to 4 times of chromium, when the content of Mo is 0.3%��0.5%, not only has good anti-H 2 S cracking performance, and use cost is relatively low.
The content of Al is 0.04%��0.08%, and owing to Al is the main deoxidant element in steel alloy, Al maxima solubility in austenite is 0.6%, and Al is only capable of faintly increasing quenching degree after dissolving in austenite; When the content of Al is higher in steel alloy, can cause in steel alloy to be mingled with and increase, and then reduce the toughness of steel alloy, hardenability and hydrogen sulfide corrosion resistance energy. When in steel alloy, the content of Al is 0.04%��0.08%, Al can be fully immersed in austenite, can not only increase austenitic quenching degree, and keep the hydrogen sulfide corrosion resistance energy of steel alloy.
Ni is the essential element promoting steel alloy to form stable austenite tissue, it is possible to the critical temperature starting to precipitate out F when iron-carbon alloy is cooled down in austenite is minimum, simultaneously so that the increase of cold crack sensitivity coefficient is minimum. During content 0%��0.3% of Ni, it is possible to coexist with Ni and the Nb in steel alloy, V, make the phase transition temperature of steel alloy reduce, promote the formation of fine precipitates, reduce steel alloy refining cost. The content 0%��0.3% of Ni, it is possible to prevent the suction hydrogen that Ni too high levels causes, and then can effectively reduce the sulfide fracture sensitivity of steel alloy.
The content of Nb is 0.04%��0.08%, Nb can refining alloy steel crystal grain, reduce steel alloy superheated susceptivity, reduce steel alloy temper brittleness, improve steel alloy intensity.
Nb can the Main Tissues ferrite of the normalizing of refining alloy steel and annealing, increase the ferritic resistance of deformation of high temperature, the deformation (especially the deformation of MnS) of field trash during rolling, increase along with content of niobium, the length-width ratio of MnS increases, and the sensitivity of HIC (anti-hydrogen induced cracking) increases.When content of niobium is less than 0.037%, Nb (CN) particle is very tiny, and now HIC crackle mainly appears on elongated MnS top, decreases the inhomogeneities of ferritic structure, is effectively improved the performance of steel resisting sulfide corrosion.
V is the excellent deoxidizer of steel, vanadium can fining ferrite grains, improve the intensity of steel alloy and toughness. Vanadium can form carbide with carbon, and when High Temperature High Pressure, carbide can improve resistant to hydrogen corrosive power, improves the cementite (Fe precipitated out when iron-carbon alloy is by the solidification of metastable equilibrium system and cooling transformation3C type carbide) fusing point, hardness and wearability. During the too high levels of V, it is easy to making the welding position of steel alloy produce fragility, therefore the content of V can not be too high, controls 0.08%��0.12%.
Cu can form protecting film in steel, and protecting film can hinder hydrogen atom to spread in steel, and then improves the resistance against hydrogen cracking performance of steel; During copper too high levels, during hot-working, steel alloy easily produces hot-short, and therefore the content of copper can not be too high, controls less than 0.2%.
Rare earth can crystal grain thinning, under controlled rolling, appropriate rare earth can make rolling state steel be granular bainite microstructure. In austenitic area, rare earth makes the stage of incubation that niobium carbide precipitates out extend, and makes beginning and the finish-time interval increasing of dynamic recrystallization. Rare earth and the arsenic impurities of low melting point, antimony etc. are combined to high melting compound and are dissolved in ferrite, purify crystal boundary, and then reduce boundary defect, contribute to alleviating hydrogen sulfide corrosion. Rare earth also has fabulous sulphur removal.
Steel adds rare earth, the silicate, aluminium oxide, oxygen in the field trash such as aluminium chlorhydrate and Manganese monosulfide. and the sulfur that exist in steel can be replaced, form rare earth compound, rare earth compound is unlikely to deform when hot-working, remain in that tiny spherical or spindle, relatively evenly it is distributed in steel, eliminates being mingled with in strip MnS etc. along steel rolling directional spreding being originally present, it is achieved the effective control to inclusion morphology.
The Denaturation of field trash is had the process of a gradual change by rare earth with the increase of content. Containing a small amount of rare earth in steel, just it is observed that the MnS containing rare earth thicker, that shortened on steel, continue to increase with rare earth composition, increase gradually containing spherical rare-earth sulfide, and with field trashes such as coccoid RES, when steel middle rare earth reaches certain value, strip MnS field trash is just wholly absent, the MnS field trash of about more than 90% can become tiny spherical or imitative capitate granule, more uniform distribution, elongate strip MnS can be overcome to be mingled with produced directivity, overcome the lamellar tearing of welding heat affected zone. The thermal coefficient of expansion of re inclusion and being similar to of steel, it is possible to avoid around field trash, producing bigger additional stress during steel heat processing cooling, improve the fatigue strength of steel. Rare earth can suppress Austenite Grain Growth in steel, and crystal boundary is had pinning effect by tiny spherical rare-earth field trash, can hinder the migration of crystal boundary, thus inhibiting grain growth.
In the embodiment of the present invention, rare earth includes the La of 20%��40%, the Ce of 40%��50%, the Pr of Nd and 1% of 15%��20%��5%, can effectively control the state of field trash shape, suppress Austenite Grain Growth in steel so that the crystal grain ratio of the rare earth alloy steel arrived is more uniform, and Performance comparision is good.
S, P: sulfur and phosphorus are all the harmful elements in steel, S��0.005% in the present embodiment, P��0.018%, it is possible to increase the corrosion resistance of rare earth alloy steel.
Below, by 7 embodiments, the present invention is elaborated:
Ginseng is shown in Table 1, for the rare earth alloy steel that component is different.
Table 1, the content of each component in embodiment 1,2,3,4,5,6,7
Ginseng is shown in Table 2, and the yield strength of the rare earth alloy steel that the formula of employing embodiment 1 obtains is 390MPa, and tensile strength is 540MPa, and the contraction percentage of area is 65%, and elongation after fracture is 32%.
The yield strength of the rare earth alloy steel that the formula of employing embodiment 2 obtains is 380MPa, and tensile strength is 565MPa, and the contraction percentage of area is 63%, and elongation after fracture is 31%.
Table 2, the mechanical property of the steel alloy that embodiment 1,2 is made
Ginseng is shown in Table 3, and sample 1 is the steel that the trade mark is 15Cr2AlMo rare earth, and sample 2 is the steel of Q245R for board, and sample 3 is the rustless steel of 304 for the trade mark, and sample 4 is the steel (hereinafter referred to as RE300) of synthesis in the embodiment of the present invention. In table 3, the unit of average corrosion rate is mg/cm2.h��
The contrast of table 3 embodiment of the present invention and other materials homogeneous corrosion performance
When 35 DEG C, sample 1,2,3 and RE300 being respectively put in the liquor ferri trichloridi that concentration is 6%, deposit 24h and carry out immersion corrosion, the average corrosion rate obtaining RE300 is 2.36mg/cm2.h, lower than other all of samples.
When 155 DEG C, rare earth alloy steel is put into the MgCl that concentration is 45%2In solution, taking out, obtain smooth surface after carrying out the boiling immersion corrosion test of 72h, there is not the form such as pitting corrosion, knife line attack in the surface of rare earth alloy steel, and for homogeneous corrosion, measurement obtains RE300 at MgCl2In average corrosion rate be 0.062mg/cm2.h, lower than sample 1,2, RE300, there is good anti-chlorine ion stress corrosion ability.
Temperature be 70 DEG C, concentration be the H of 50%2SO4In system, the corrosion rate of RE300 is lower than sample 1,2,3.
Temperature be 80 DEG C, concentration be 3% HCl system in, temperature is 100 DEG C, concentration is the H of 1000ppm2In S system, the corrosion rate of RE300 is lower than sample 1,2,3. At H2In S system, although the corrosion rate of RE300 is higher than stainless steel 304, but, stainless steel 304 relatively costly, sulfuric acid corrosion resistant and ferric chloride corrosive power are poor, there is stress corrosion harm simultaneously, owing to the comparison of ingredients of oil and industrial chemicals is complicated, usually contain sulfide, hydrogen, Wet H2S environment and chloride ion, if Steel for Petrochemicai Equipment is corroded by any of which composition, device damage can be caused, therefore, need to select the steel being prevented from the corrosion of any one composition to prepare Steel for Petrochemicai Equipment, RE300 in the embodiment of the present invention disclosure satisfy that above-mentioned requirements, therefore, RE300 can be used in preparation can the Steel for Petrochemicai Equipment of life-time service, extend the service life of petrochemical equipment, reduce the use cost of petrochemical equipment.
HIC test performs according to GB/T8650-2006 " pipe line steel and steels for pressure vessel use resistance against hydrogen cracking assessment method ", and test(ing) medium is 5% glacial acetic acid+5% sodium-chloride water solution that hydrogen sulfide is saturated. SSCC (hydrogen sulfide splitting) test performs according to GB/T4157-2006 " metal is anti-specific form environmental cracking laboratory test in hydrogen-sulfide environmental ", and test(ing) medium is 5% glacial acetic acid+5% sodium-chloride water solution that hydrogen sulfide is saturated.
Table 4, the steel plate of the embodiment of the present invention and other materials hydrogen sulfide corrosion resistance can contrast
Ginseng is shown in Table 4, sample 5,6,7 corresponding thickness respectively be the RE300 steel plate of 12mm, 24mm, 30mm, sample 8 and sample 9 for thickness be 20, the hydrogen sulfide corrosion resistant steel plate of steel grade rank respectively Q245R, Q345R.
Sample 5,6,7 in the fabrication process, the technique all adopting normalizing and tempering, HIC test result is: hydrogen blister situation do not occur, crack length rate, crack thickness rate and crack-sensitivity rate are 0%; SSCC test result is 320MPa.
In the fabrication process, only with normalizing process, HIC test result is sample 8: do not occur hydrogen blister situation, crack length rate be 3%, crack thickness rate be 1%, crack-sensitivity rate be 0%; SSCC test result is 247MPa.
In the fabrication process, only with normalizing process, HIC test result is sample 9: do not occur hydrogen blister situation, crack length rate be 5%, crack thickness rate be 2%, crack-sensitivity rate be 2%; SSCC test result is 247MPa.
HIC and the SSCC result of sample 5,6,7 is superior to sample 8,9, and therefore, the steel plate of the embodiment of the present invention not only resistance against hydrogen cracking ability is relatively strong but also anti-H 2 S stress corrosion cracking ability is stronger.
Table 5, the steel plate of the embodiment of the present invention and field trash in other materials and grain size contrast
Ginseng is shown in Table 5, and contains only a small amount of A class and B type impurity in sample 5,6,7, and without C class, D class and DS type impurity, and grain size is 9 grades.
The grain size of sample 8,9 is 8 grades, less than 9. A class and the inclusion content of B class in sample 8,9 are all higher than sample 5,6,7, and containing C class, D class and DS type impurity in sample 8, containing C type impurity in sample 9.
The steel plate of table 6 embodiment of the present invention and the stretching of other materials, impact property contrast
Ginseng is shown in Table 6, and the RE300 steel plate tensile strength at normal temperatures that thickness is 20mm is 540Mpa, and the tensile strength under 450 DEG C of conditions is 427Mpa, yield strength is 400Mpa, and percentage elongation is 32%, and the ballistic work at 0 DEG C is 230J, ballistic work at-30 DEG C is 192J, and hardness number is 143HB.
RE300 steel plate and thickness are the hydrogen sulfide corrosion resistant steel plate of 20mm, steel grade rank respectively Q245R, Q345R, and middle temperature steel plate of pressure vessel 15CrMoR compares, and the tensile strength under RE300 tensile strength at normal temperatures, 450 DEG C of conditions is higher; Meanwhile, the shock resistance weight bearing power of RE300 is stronger.
Table 7, the steel pipe of the embodiment of the present invention and the stretching of other materials, impact property contrast
Ginseng is shown in Table 7, the room temperature tensile strength of the special seamless steel pipe 08Cr2AlMo of heat exchanger is 470Mpa, yield strength is 325Mpa, tensile strength is 326Mpa at 450 DEG C, percentage elongation is the ballistic work at 31%, 0 DEG C is 93J, ballistic work at-30 DEG C is 42J, and hardness number is 112HB.
The room temperature tensile strength of seamless steel pipe 10 (HSC) is 421Mpa, yield strength is 317Mpa, tensile strength is 265Mpa at 450 DEG C, percentage elongation is the ballistic work at 32%, 0 DEG C is 82J, ballistic work at-30 DEG C is 38J, and hardness number is 118HB.
The RE300 steel pipe of the embodiment of the present invention, its room temperature tensile strength is 618Mpa, higher than the 30% of 08Cr2AlMo and 10 (HSC); RE300 steel pipe tensile strength at 450 DEG C is 453Mpa, higher than the 50% of 08Cr2AlMo and 10 (HSC).
The percentage elongation of RE300 steel pipe is 34.5%, and higher than the percentage elongation of 08Cr2AlMo and 10 (HSC), the deformation adaptability of RE300 steel pipe is better.
RE300 steel pipe ballistic work at 0 DEG C is 228J, ballistic work at-30 DEG C is 205J, far above the analog value of the special seamless steel pipe 08Cr2AlMo of heat exchanger and seamless steel pipe 10 (HSC), therefore the low-temperature impact toughness of RE300 steel pipe is far above the special seamless steel pipe 08Cr2AlMo of heat exchanger and seamless steel pipe 10 (HSC).
The hardness number of RE300 steel pipe is 148HB, and higher than the special seamless steel pipe 08Cr2AlMo of heat exchanger and seamless steel pipe 10 (HSC), therefore, the wearability of RE300 steel pipe is better.
The present invention is not limited to above-mentioned embodiment, for those skilled in the art, under the premise without departing from the principles of the invention, it is also possible to make some improvements and modifications, and these improvements and modifications are also considered as within protection scope of the present invention. The content not being described in detail in this specification belongs to the known prior art of professional and technical personnel in the field.
Claims (9)
1. a corrosion-proof rare earth steel alloy, it is characterized in that: by mass percentage, this rare earth alloy steel includes the C of 0.03%��0.08%, the Si of 0.25%��0.45%, the Mn of 0.42%��0.55%, the P of 0.001%��0.014%, the S of 0.001%��0.0035%, the Cr of 1.82%��1.98%, the Ni of 0.005%��0.2%, the Mo of 0.32%��0.48%, the Al of 0.05%��0.07%, the V of 0.09%��0.11%, the Nb of 0.05%��0.07%, the Cu of 0.07%��0.15%, the rare earth of 0.007%��0.020%, surplus is Fe, rare earth includes the La of 20%��40%, the Ce of 40%��50%, the Pr of Nd and 1% of 15%��20%��5%, and described rare earth alloy steel is through normalizing at the temperature of 950 �� 10 DEG C, obtain after tempering at the temperature of 700 �� 10 DEG C, this rare earth alloy steel be organized as ferrite+sorbite tissue.
2. corrosion-proof rare earth steel alloy as claimed in claim 1, it is characterized in that: by mass parts, described rare earth alloy steel includes the C of 0.03%��0.05%, the Si of 0.30%��0.40%, the Mn of 0.45%��0.52%, the P of 0.001%��0.012%, the S of 0.001%��0.003%, the Cr of 1.85%��1.95%, the Ni of 0.005%��0.15%, the Mo of 0.35%��0.45%, the Al of 0.055%��0.65%, the V of 0.095%��0.105%, the Nb of 0.055%��0.065%, the Cu of 0.07%��0.10%, the rare earth of 0.008%��0.015%, surplus is Fe, rare earth includes the La of 20%��40%, the Ce of 40%��50%, the Pr of Nd and 1% of 15%��20%��5%.
3. corrosion-proof rare earth steel alloy as claimed in claim 2, it is characterised in that: the content of described rare earth alloy steel middle rare earth is 0.01%.
4. the corrosion-proof rare earth steel alloy as according to any one of claims 1 to 3, it is characterised in that: described rare earth include 30% La, 48% Ce, 19% the Pr of Nd and 3%.
5. the corrosion-proof rare earth steel alloy as according to any one of claims 1 to 3, it is characterised in that: the yield strength of described rare earth alloy steel is 380��390MPa, and tensile strength is 540��565MPa.
6. the corrosion-proof rare earth steel alloy as according to any one of claims 1 to 3, it is characterised in that: the contraction percentage of area of described rare earth alloy steel is 63%��65%, and elongation after fracture is 31%��32%, and percentage elongation is 34.5%.
7. the corrosion-proof rare earth steel alloy as according to any one of claims 1 to 3, it is characterised in that: described grain size is more than 6 grades, and the summation of nonmetallic inclusion is less than 4.0.
8. the corrosion-proof rare earth steel alloy as according to any one of claims 1 to 3, it is characterised in that: described rare earth alloy steel ballistic work at 0 DEG C is 228J, ballistic work at-30 DEG C is 205J.
9. the method preparing corrosion-proof rare earth steel alloy, it is characterised in that comprise the following steps:
A, raw material is put in electric furnace refine, obtain molten steel;Molten steel is transferred to external refining bag and carries out external refining and vacuum outgas, adding aluminum in degassed backward steel is 0.05%��0.08% to the content of aluminum in steel, add rare earth and keep little argon stirring more than 15min, the content of rare earth is 0.007%��0.020%, rare earth includes the La of 20%��40%, the Ce of 40%��50%, the Pr of Nd and 1% of 15%��20%��5%, adjusting the content of C in ladle is 0.03%��0.08%, the content of Si is 0.25%��0.45%, the content of Mn is 0.42%��0.55%, the content 0.001%��0.014% of P, the content 0.001%��0.0035% of S, the content of Cr is 1.82%��1.98%, the content 0.005%��0.2% of Ni, the content of Mo is 0.32%��0.48%, the content of Al is 0.05%��0.07%, the content of V is 0.09%��0.11%, the content of Nb is 0.05%��0.07%, the content 0.07%��0.15% of Cu,
The casting molding of B, bull ladle obtains electrode billet, electrode billet is carried out electroslag remelting, obtain rare earth alloy steel electroslag ingot, nearly finished product is obtained by after electroslag ingot hot-working, roughing, nearly finished product is carry out 700 �� 10 DEG C of temper after 950 �� 10 DEG C of normalized treatment through temperature, obtaining rare earth alloy steel finished product then through polish, the organizational structure of described rare earth alloy steel finished product is ferrite+sorbite tissue.
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