CN111705262A - Magnesium-containing X65 pipeline steel with excellent acid resistance and production method thereof - Google Patents
Magnesium-containing X65 pipeline steel with excellent acid resistance and production method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/0006—Adding metallic additives
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/0056—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00 using cored wires
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/10—Handling in a vacuum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B2015/0057—Coiling the rolled product
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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Abstract
A magnesium-containing X65 pipeline steel with excellent acid resistance comprises the following components in percentage by weight: c: 0.03 to 0.05%, Si: 0.17-0.20%, Mn: 0.40 to 0.70% of Ni: 0.12-0.15%, Cr: 0.45-0.48%, Mo: 0.10-0.15%, Mg: 0.002-0.004%, Nb: 0.06-0.09%, Ti: 0.01-0.02%, P is less than or equal to 0.008%, and S is less than or equal to 0.010%; the production method comprises the following steps: smelting in a converter, carrying out Mg treatment in vacuum, and then pouring into a blank; heating a casting blank; rough rolling; fine rolling; laminar cooling; and (4) coiling. The invention ensures Rt0.5420~440MPa，RmIs 480 to 500MPa, Rt0.5/RmUnder the premise of less than or equal to 0.90, the elongation percentage A after fracture is enabled50mmNot less than 20 percent and-20 ℃ impact energy KV2The shear surface ratio DWTT SA of the fracture is more than or equal to 200J and less than or equal to 90 percent at minus 15 ℃, the hardness value HV10 is less than or equal to 180 percent, the hydrogen induced crack sensitivity rates CLR, CTR and CSR do not exceed 0.05 percent in NACE A solution, and sulfide stress cracking does not occur under the stress loading rate of 0.9.
Description
Technical Field
The invention relates to pipeline steel and a production method thereof, in particular to magnesium-containing X65 acid corrosion resistant pipeline steel and a production method thereof.
Background
With the development of economic society of China, the oil and gas resource demand is huge, and the state is vigorously building oil and gas pipe networks. But oil and gas resources are often rich in H2S and other acidic media, pipeline steel and H in the process of oil and gas transportation2The S phase contacts and reacts to generate Hydrogen Induced Cracking (HIC) and hydrogen Sulfide Stress Corrosion Cracking (SSCC), finally causing the failure of pipeline steel, resulting in larger economic loss and environmental pollution. Aiming at the H content in the transportation in order to ensure the reliability of oil and gas pipe networks in China2The pipeline of S and other acidic oil and gas must use acid-resistant pipeline steel, and the highest steel grade of the acid-resistant pipeline applied in large batch at present is X65 MS.
The inclusion is an important factor influencing the hydrogen sulfide corrosion resistance of the pipeline steel, and the cracks are generally formed from non-metallic inclusionWhere they grow and cross-connect with each other. Non-metallic inclusions MnS and Al in the Steel2O3The higher the amount and grade, the worse the hydrogen sulfide corrosion resistance. At present, in order to solve the problem, namely reducing inclusions in steel and improving the hydrogen sulfide corrosion resistance of pipeline steel, the technical field basically adopts the technical measures of carrying out ultralow desulfurization treatment in the production of acid-resistant pipeline steel, which not only leads to high production cost, but also has relatively high cracking rate, and according to statistics, the cracking rate is generally 2-10%.
In order to reduce the production cost of the acid-resistant pipeline steel on the premise of ensuring the service performance, the technical personnel modify inclusions in the steel by magnesium treatment so as to reduce the ultra-low desulfurization treatment cost and improve the hydrogen sulfide corrosion resistance of the pipeline steel. As retrieved:
chinese patent application No. CN201710659944.3 discloses "a low-cost X65 pipeline steel based on magnesium treatment and its manufacturing method". The weight percentage of the chemical components is as follows: c: 0.07-0.09%, Si: 0.1-0.3%, Mn: 1.35-1.45%, S is less than or equal to 0.006%, P is less than or equal to 0.015%, Nb: 0.035 to 0.045%, Ti: 0.010-0.025%, Mg: 0.0010-0.0030%, Al: 0.020-0.030 percent of N, less than or equal to 0.006 percent of N, and the balance of Fe and inevitable impurities. The metallographic structure of the generated hot-rolled steel plate is fine-grained ferrite, acicular ferrite and pearlite, and the elongation A after fracture of the hot-rolled steel plate with the thickness of 10.0-15.0 mm is more than or equal to 24%. However, the addition of C, Mn is high, which causes the structure segregation of the produced X65 pipeline steel, and Al is added for deoxidation in the steel2O3The inclusion amount is large, and the HIC resistance and the SSCC resistance are not favorable.
The Chinese patent application No. 201110100872.1 discloses a preparation method of easily-welded high-strength and high-toughness X80 pipeline steel treated by magnesium, which comprises the following chemical components in percentage by mass: 0.03 to 0.06% of C, 0.1 to 0.3% of Si, 1.6 to 1.8% of Mn, 0.001 to 0.01% of Mg, 0.010 to 0.03% of Ti, 0.02 to 0.04% of Al, 0.02 to 0.06% of Nb, 0.1 to 0.5% of Cr, 0.1 to 0.4% of Mo, and 0.3 to 0.5% of Ni; 0.1-0.5% of Cu, less than or equal to 0.012% of P, less than or equal to 0.003% of S, wherein Ti/Mg is controlled between 1-30, and the balance is Fe; rolling and cooling are controlled to obtain the excellent structure of the acicular ferrite. The reference also uses a high Mn composition design and uses Al deoxidation to produce X80 pipeline steel with poor HIC and SSCC resistance.
Chinese patent application No. 201410276157.7 discloses "a HIC-resistant hot-rolled steel sheet and a magnesium treatment smelting method thereof", which adopts 0.06 wt% -0.20 wt% of C, 0.10 wt% -0.50 wt% of Si, 0.4 wt% -1.6 wt% of Mn, less than or equal to 0.25 wt% of P, less than or equal to 0.010 wt% of S, less than or equal to 0.06 wt% of Nb, less than or equal to 0.15 wt% of V, 0.0001 wt% -0.020 wt% of Mg and Ti, less than 0.010 wt% of Als, and the balance of Fe and inevitable impurities. The invention suppresses the formation of a band-shaped structure in a steel sheet and improves the performance of the steel sheet. However, this document does not describe steel grade and HIC resistance.
In summary, in the prior art, the C, Mn composition is designed to be high to ensure the strength of the steel, so that the microalloying is carried out by adding less Nb. In steel making, in order to reduce the oxygen content in steel, Al is generally used for deoxidation to generate Al in molten steel2O3And (4) inclusion. Studies have shown that higher C, Mn is prone to tissue segregation, and that hydrogen induced cracks often develop and propagate along tissue segregation. Hydrogen induced cracking in spherical Al2O3The inclusion is generated and the non-metallic inclusion Al2O3The greater the amount, the greater the susceptibility to hydrogen induced cracking. Therefore, the existing component system is not good for the HIC and SSCC resistance of the pipeline steel.
Disclosure of Invention
Aiming at the defects of the prior art, the invention provides a method for ensuring the mechanical property yield strength Rt0.5420 to 440MPa, tensile strength Rm480 to 500MPa, and a yield ratio Rt0.5/RmUnder the premise of less than or equal to 0.90, the elongation percentage A after fracture is enabled50mmNot less than 20 percent and-20 ℃ impact energy KV2The shear surface ratio DWTT SA of the fracture is more than or equal to 200J and less than or equal to 90 percent at minus 15 ℃, the hardness value HV10 is less than or equal to 180 percent, the hydrogen induced crack sensitivity rates CLR, CTR and CSR do not exceed 0.05 percent in NACE A solution, and sulfide stress cracking does not occur under the stress loading rate of 0.9.
The technical measures for realizing the purpose are as follows:
the magnesium-containing X65 pipeline steel with excellent acid resistance comprises the following components in percentage by weight: c: 0.03 to 0.05%, Si: 0.17-0.20%, Mn: 0.40 to 0.70%, Ni: 0.12-0.15%, Cr: 0.45-0.48%, Mo: 0.10-0.15%, Mg: 0.002-0.004%, Nb: 0.06-0.09%, Ti: 0.01-0.02% of Fe, less than or equal to 0.008% of P, less than or equal to 0.010% of S, and the balance of Fe and inevitable impurities; the metallographic structure is acicular ferrite, the grain size is more than or equal to 10, and the level of inclusions is less than or equal to 0.5.
Preferably: the Ni content by weight percentage is as follows: 0.130-0.145%.
Preferably: the Nb content is 0.072-0.085 wt%.
The method for producing the magnesium-containing X65 pipeline steel with excellent acid resistance comprises the following steps:
1) smelting in a converter, carrying out Mg treatment in vacuum, and then pouring into a blank; adding Mg wires into the steel ladle at a wire feeding speed of 2-5 m/s during vacuum treatment, wherein the adding amount meets the principle of design content;
2) heating a casting blank, and controlling the heating temperature of the casting blank to be 1200-1230 ℃;
3) carrying out rough rolling, and controlling the rough rolling starting temperature to be 1050-1100 ℃ and the rough rolling finishing temperature to be 950-1000 ℃; the total yield is 60-70%;
4) carrying out finish rolling, and controlling the start rolling temperature of the finish rolling to be 880-910 ℃ and the finish rolling temperature of the finish rolling to be 850-880 ℃; the accumulated reduction rate of finish rolling is not less than 60%, and the thickness of a finish rolled plate is 12-20 mm;
5) carrying out laminar cooling, and cooling to the coiling temperature at the cooling speed of 23-26 ℃/s;
6) coiling is carried out, and the coiling temperature is controlled to be 520-550 ℃.
Preferably: the rough rolling finishing temperature is 962-993 ℃.
Preferably: the initial rolling temperature of the finish rolling is 880-900 ℃, and the final rolling temperature of the finish rolling is 855-875 ℃.
Preferably: the coiling temperature is 525-543 ℃.
The mechanism and action of each component and main process in the invention
Carbon (C): carbon is the most economic and basic strengthening element of pipeline steel, and can reduce the addition of other precious alloys. However, too high carbon has a negative effect on ductility, low temperature impact toughness, weldability, hydrogen sulfide corrosion resistance, etc. of the pipeline steel. The carbon content of the invention is limited to 0.03-0.05%.
Silicon (Si): silicon mainly plays roles of deoxidation and solid solution strengthening, but excessive addition of silicon can cause reduction of plasticity, toughness and weldability of the steel. The silicon content of the invention is limited to 0.17-0.20%.
Manganese (Mn): the addition of a proper amount of manganese can improve the hardenability of the steel pipe, and simultaneously play a role in solid solution strengthening to make up for the strength reduction caused by low carbon or ultra-low carbon. However, when the Mn content exceeds 1.0%, the structure is likely to segregate, and a band-shaped structure is formed, which is disadvantageous in the hydrogen sulfide corrosion resistance of the line pipe steel. The content of manganese in the invention is limited to 0.40-0.70%.
Nickel (Ni): the nickel can improve the corrosion resistance of the steel and effectively improve the stability of the strength performance of the steel plate. But nickel is more costly. The content of nickel in the invention is limited to 0.12-0.15%, and the content of Ni in percentage by weight is preferably 0.130-0.145%.
Chromium (Cr): chromium is an important element for increasing the hardenability of steel and can be enriched in corrosion product films, reducing the local corrosion sensitivity of steel. However, the addition of chromium in large amounts reduces the toughness and weldability of the pipeline steel. The chromium content of the invention is limited to 0.45-0.48%.
Molybdenum (Mo): molybdenum can lower the transformation temperature, inhibit the formation of massive ferrite and promote the transformation of acicular ferrite. The addition of molybdenum can improve the pitting corrosion resistance of the steel and improve the SSCC resistance of the steel. The molybdenum can improve the strength of the steel pipe when the UOE is used for manufacturing the pipe, and compensate the strength loss caused by the Bauschinger effect. Molybdenum can degrade the weldability. The content of molybdenum in the invention is limited to 0.10-0.15%.
Magnesium (Mg): the addition of magnesium can refine inclusions and the grain structure in the steel. Magnesium has strong deoxidizing capacity and can quickly reduce the oxygen content in steel to generate magnesium oxide. The critical nucleation radius of magnesium oxide in molten steel is small, so that the magnesium oxide is easy to nucleate and has high nucleation rate. A large number of fine magnesium oxide particles in the molten steel become nucleation particles of other inclusions precipitated later, so that more and finer inclusions are formed in the steel. The large amount of composite inclusions which are distributed in a fine and dispersed mode are used as ferrite crystal nuclei to induce the test steel to form a fine acicular ferrite structure. The content of magnesium in the invention is limited to 0.002-0.004%.
Niobium (Nb): niobium can obviously refine grains, plays a role in precipitation strengthening, and enables the steel to have high strength and high toughness. The corrosion performance of the low-alloy steel can be effectively improved by adding niobium into the low-alloy steel. According to the invention, higher Nb is added, so that the strength can be improved, and the strength loss caused by low C, Mn component design can be compensated. However, if it is higher than the range defined in the present application, it is disadvantageous in weld impact toughness. If the content is less than the above range, the strength and toughness of the steel may be insufficient. Therefore, the content of Nb is limited to 0.06-0.09%, and the content of Nb is preferably 0.072-0.085% by weight.
Titanium (Ti): the titanium is beneficial to deoxidizing the steel, reduces inclusions in the steel and improves the impact toughness of the steel. However, when the titanium content exceeds a certain value, TiN particles coarsen, TiC exhibits a precipitation strengthening effect, and the low-temperature toughness of the steel is reduced. The content of vanadium in the invention is limited to 0.01-0.02%.
Phosphorus (P): phosphorus is a harmful element in steel, and a ferrite-pearlite banded structure containing phosphorus segregation is formed in the steel, so that the HIC sensitivity is enhanced. However, the fine and dispersed composite inclusions generated after the magnesium is added serve as non-uniform nucleation cores, and the generation of banded structures is favorably inhibited. In order to reduce the dephosphorization cost, the invention adopts a higher phosphorus content of less than or equal to 0.008 percent.
Sulfur (S): the sulfur element can promote the generation of HIC and is a very harmful element, and MnS inclusions generated by the sulfur element and Mn are the most easily nucleated positions of HIC. When the sulfur content in the steel is less than 0.002%, the HIC is significantly reduced. However, the magnesium is added into the steel, so that the MnS can be generated into MgS-MnS composite inclusion which is harmless to the HIC performance, and in order to reduce the ultra-low desulfurization cost, the invention adopts the higher sulfur content which is less than or equal to 0.010 percent.
The invention carries out deoxidation by adding Mg to replace AlInhibiting the band-shaped structure and preventing harmful Al2O3And (4) generating the inclusions. On one hand, the addition of magnesium changes strip-shaped MnS into fine MgS-MnS composite inclusions, and reduces the sensitivity of HIC and SSCC. On the other hand, a fine acicular ferrite structure is induced, and the structure has an effect of inhibiting crack propagation. Thus, the strength, toughness and HIC and SSCC resistance of the steel are improved. By adopting the design with low C, Mn components, the structure segregation is reduced, and the HIC and SSCC performances are improved, but the strength of the steel is reduced. Microalloying by adding higher Nb made up for the strength loss due to low C, Mn.
The heating temperature of the casting blank is 1200-1230 ℃, because the temperature range ensures that coarse TiN, TiC and other particles in the casting blank are fully dissolved in austenite grains, and fine and dispersed TiN, TiC and other particles are separated out from a steel plate after rolling, thereby achieving the effect of precipitation strengthening.
The invention controls the initial rolling temperature of the rough rolling to be 1050-1100 ℃ and the finishing temperature of the rough rolling to be 950-1000 ℃, because the rough rolling process is carried out above the austenite recrystallization temperature, the crystallization temperature of the invention is about 950 ℃ under the component system.
The invention controls the initial rolling temperature of finish rolling to be 880-910 ℃, and the final rolling temperature of finish rolling to be 850-880 ℃; the accumulated reduction rate of finish rolling is not less than 60% because ferrite (Ar) is precipitated from austenite in the finish rolling process3) The temperature is increased, ferrite nucleation particles are added due to the addition of Mg, and the precipitation strengthening of TiN and TiC is facilitated due to the higher finish rolling temperature.
The cooling to the coiling temperature of 520-550 ℃ is controlled at a cooling rate of 23-26 ℃/s, because the formation of acicular ferrite structure is facilitated by a higher cooling rate, and the growth of ferrite structure can be inhibited by a lower coiling temperature.
Compared with the prior art, the invention ensures the mechanical property yield strength Rt0.5420 to 440MPa, tensile strength Rm480 to 500MPa, and a yield ratio Rt0.5/RmUnder the premise of less than or equal to 0.90, the elongation percentage A after fracture is enabled50mmNot less than 20 percent and-20 ℃ impact energy KV2Shearing fracture at-15 deg.C of not less than 200JThe area ratio DWTT SA is more than or equal to 90 percent, the hardness value HV10 is less than or equal to 180 percent, the hydrogen induced crack sensitivity rates CLR, CTR and CSR do not exceed 0.05 percent in NACE A solution, and sulfide stress cracking does not occur under the stress loading rate of 0.9.
Drawings
FIG. 1 is a metallographic structure diagram of a steel of the present invention.
Detailed Description
The present invention is described in detail below:
table 1 is a list of values of chemical components of each example and comparative example of the present invention;
table 2 is a list of values of main process parameters in each example and comparative example of the present invention;
table 3 shows the transverse main mechanical property detection statistical table of each embodiment and comparative example of the invention;
table 4 is a statistical table of HIC resistance of each example and comparative example of the present invention
Table 5 is a statistical table of SSCC resistance performance of each example and comparative example of the present invention.
Each example was produced according to the following procedure:
1) smelting in a converter, carrying out Mg treatment in vacuum, and then pouring into a blank; adding Mg wires into the steel ladle at a wire feeding speed of 2-5 m/s during vacuum treatment, wherein the adding amount meets the principle of design content;
2) heating a casting blank, and controlling the heating temperature of the casting blank to be 1200-1230 ℃;
3) carrying out rough rolling, and controlling the rough rolling starting temperature to be 1050-1100 ℃ and the rough rolling finishing temperature to be 950-1000 ℃; the total yield is 60-70%;
4) carrying out finish rolling, and controlling the start rolling temperature of the finish rolling to be 880-910 ℃ and the finish rolling temperature of the finish rolling to be 850-880 ℃; the accumulated reduction rate of finish rolling is not less than 60%, and the thickness of a finish rolled plate is 12-20 mm;
5) carrying out laminar cooling, and cooling to the coiling temperature at the cooling speed of 23-26 ℃/s;
6) coiling is carried out, and the coiling temperature is controlled to be 520-550 ℃.
TABLE 1 list of chemical compositions (wt%) of inventive and comparative examples
TABLE 2 tabulation of values of main process parameters of each example and comparative example of the present invention
TABLE 3 statistical table for transverse main mechanical property test of each example and comparative example of the present invention
TABLE 4 statistical tables of HIC resistance of examples of the present invention and comparative examples
Table 4 shows the results of Evaluation of HIC Resistance using the solution A according to NACE TM 0284-2016 Evaluation of analysis of Pipeline and Pressure vessel steps for Resistance to Hydrogen-Induced Cracking, wherein the Hydrogen crack susceptibility CLR, CTR and CSR of the present invention are all 0%, and no Hydrogen bubbles are present on the surface.
TABLE 5 statistical Table of SSCC resistance of examples of the invention and comparative examples
Table 5 shows NACE TM 0177-n H2According to the evaluation result of the SSCC resistance by adopting the solution A in the SEnvironments standard, the invention has no stress cracking under the stress loading rates of 0.72, 0.8 and 0.9.
The above examples are merely preferred examples and are not intended to limit the embodiments of the present invention.
Claims (7)
1. The magnesium-containing X65 pipeline steel with excellent acid resistance comprises the following components in percentage by weight: c: 0.03 to 0.05%, Si: 0.17-0.20%, Mn: 0.40 to 0.70%, Ni: 0.12-0.15%, Cr: 0.45-0.48%, Mo: 0.10-0.15%, Mg: 0.002-0.004%, Nb: 0.06-0.09%, Ti: 0.01-0.02% of Fe, less than or equal to 0.008% of P, less than or equal to 0.010% of S, and the balance of Fe and inevitable impurities; the metallographic structure is acicular ferrite, the grain size is more than or equal to 10, and the level of inclusions is less than or equal to 0.5.
2. The magnesium-containing X65 pipeline steel with excellent acid resistance as claimed in claim 1, wherein: the Ni content by weight percentage is as follows: 0.130-0.145%.
3. The magnesium-containing X65 pipeline steel with excellent acid resistance as claimed in claim 1, wherein: the Nb content is 0.072-0.085 wt%.
4. The method for producing the magnesium-containing X65 pipeline steel with excellent acid resistance as claimed in claim 1, which comprises the steps of:
1) smelting in a converter, carrying out Mg treatment in vacuum, and then pouring into a blank; adding Mg wires into the steel ladle at a wire feeding speed of 2-5 m/s during vacuum treatment, wherein the adding amount meets the principle of design content;
2) heating a casting blank, and controlling the heating temperature of the casting blank to be 1200-1230 ℃;
3) carrying out rough rolling, and controlling the rough rolling starting temperature to be 1050-1100 ℃ and the rough rolling finishing temperature to be 950-1000 ℃; the total yield is 60-70%;
4) carrying out finish rolling, and controlling the start rolling temperature of the finish rolling to be 880-910 ℃ and the finish rolling temperature of the finish rolling to be 850-880 ℃; the accumulated reduction rate of finish rolling is not less than 60%, and the thickness of a finish rolled plate is 12-20 mm;
5) carrying out laminar cooling, and cooling to the coiling temperature at the cooling speed of 23-26 ℃/s;
6) coiling is carried out, and the coiling temperature is controlled to be 520-550 ℃.
5. The method for producing a magnesium-containing X65 pipeline steel excellent in acid resistance as claimed in claim 4, wherein: the rough rolling finishing temperature is 962-993 ℃.
6. The method for producing a magnesium-containing X65 pipeline steel excellent in acid resistance as claimed in claim 4, wherein: the initial rolling temperature of the finish rolling is 880-900 ℃, and the final rolling temperature of the finish rolling is 855-875 ℃.
7. The method for producing a magnesium-containing X65 pipeline steel excellent in acid resistance as claimed in claim 4, wherein: the coiling temperature is 525-543 ℃.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010552764.7A CN111705262B (en) | 2020-06-17 | 2020-06-17 | Magnesium-containing X65 pipeline steel with excellent acid resistance and production method thereof |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010552764.7A CN111705262B (en) | 2020-06-17 | 2020-06-17 | Magnesium-containing X65 pipeline steel with excellent acid resistance and production method thereof |
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006283147A (en) * | 2005-04-01 | 2006-10-19 | Nippon Steel Corp | High strength steel pipe for pipe line having excellent deformation property after aging, and method for producing the same |
| CN102181802A (en) * | 2011-04-21 | 2011-09-14 | 北京科技大学 | Preparation method of easy welding high strength toughness X80 pipe line steel for magnesium treatment |
| CN106498279A (en) * | 2016-10-14 | 2017-03-15 | 武汉钢铁股份有限公司 | A kind of economical X65 pipe line steels of low Cr of anti-CO2 corrosion and production method |
| CN109385576A (en) * | 2017-08-04 | 2019-02-26 | 上海梅山钢铁股份有限公司 | A kind of inexpensive X65 pipe line steel and its manufacturing method based on magnesium processing |
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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006283147A (en) * | 2005-04-01 | 2006-10-19 | Nippon Steel Corp | High strength steel pipe for pipe line having excellent deformation property after aging, and method for producing the same |
| CN102181802A (en) * | 2011-04-21 | 2011-09-14 | 北京科技大学 | Preparation method of easy welding high strength toughness X80 pipe line steel for magnesium treatment |
| CN106498279A (en) * | 2016-10-14 | 2017-03-15 | 武汉钢铁股份有限公司 | A kind of economical X65 pipe line steels of low Cr of anti-CO2 corrosion and production method |
| CN109385576A (en) * | 2017-08-04 | 2019-02-26 | 上海梅山钢铁股份有限公司 | A kind of inexpensive X65 pipe line steel and its manufacturing method based on magnesium processing |
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