JP5223511B2 - Steel sheet for high strength sour line pipe, method for producing the same and steel pipe - Google Patents

Steel sheet for high strength sour line pipe, method for producing the same and steel pipe Download PDF

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JP5223511B2
JP5223511B2 JP2008179976A JP2008179976A JP5223511B2 JP 5223511 B2 JP5223511 B2 JP 5223511B2 JP 2008179976 A JP2008179976 A JP 2008179976A JP 2008179976 A JP2008179976 A JP 2008179976A JP 5223511 B2 JP5223511 B2 JP 5223511B2
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JP2009052137A (en
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信行 石川
豊久 新宮
仁 末吉
真 鈴木
朋裕 松島
伸夫 鹿内
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Jfeスチール株式会社
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Description

  The present invention relates to a method for producing a steel plate for line pipes having excellent strength against hydrogen-induced cracking resistance (HIC resistance) and mainly having an API standard X65 grade or higher, and a steel pipe produced using the steel plate. In particular, the present invention relates to a steel plate for a high strength sour line pipe excellent in formability at the time of cold forming and small in material variation, a manufacturing method thereof, and a steel pipe manufactured using the steel plate.

  Line pipes used for transporting crude oil and natural gas containing hydrogen sulfide have strength, toughness, weldability, hydrogen-induced crack resistance (HIC resistance), stress corrosion crack resistance (SCC resistance), etc. So-called sour resistance is required. Furthermore, in addition to these requirements, a line pipe with high dimensional accuracy is required in order to increase the work efficiency of circumferential welding of the line pipe and to perform a highly accurate structural design.

  Steel pipes manufactured by cold forming, such as UOE steel pipes, are strongly affected by material variations and residual stresses of the steel plates used for them, so using steel plates with small material variations such as strength and ductility and small residual stresses can improve dimensional accuracy. It is very effective to improve.

  Conventionally, reduction of material variation has been dealt with in terms of production management, such as strict management of steel plate manufacturing conditions, and material variation when mass-produced, especially variation in strength has been reduced, In order to improve the dimensional accuracy described above, it is necessary to reduce material variations even within the individual steel plates.

  In general, a high-strength steel plate having a tensile strength of 500 MPa or more is manufactured by accelerated cooling, and the longitudinal end portion of the steel plate is easily overcooled, and the strength of the longitudinal end portion is likely to be higher than that of the central portion. Further, due to the fact that the longitudinal end portion of the slab is overheated in the heating furnace before rolling, the strength of the longitudinal end portion may be higher than that of the central portion.

  As a measure for reducing these variations, Patent Document 1 discloses a method of reducing temperature unevenness by performing accelerated cooling in two stages and providing an air cooling section between the former stage and the latter stage cooling. It is disclosed. Although this method has a certain effect for reducing the material variation, the subsequent cooling still causes temperature unevenness in the plate length direction, and thus the material variation cannot be sufficiently eliminated.

  In this method, since the amount of softening due to tempering is generally larger in the portion with higher strength before tempering, the difference in strength after tempering is reduced, but there is a problem that the strength of the portion that does not need to be tempered also decreases. Since the tempering process takes time, the carbides are coarsened, resulting in deterioration of toughness, particularly deterioration of DWTT performance.

  As a tempering method that does not degrade toughness, Patent Document 2 discloses a method of performing rapid heating and tempering using an induction heating device installed on the same production line as the accelerated cooling device. According to this method, since the carbides generated during tempering become fine, it is possible to obtain a high toughness steel plate. However, in order to uniformly heat the steel plate, there is an effect in reducing the strength variation in the plate. Absent.

  Further, by setting the cooling stop temperature in the accelerated cooling process to 200 ° C. or less and making the microstructure before induction heating martensite, carbide refinement can be achieved by rapid heating and tempering, but the cooling stop temperature is high and the bainite is high. When it becomes a main structure, carbides may be coarsened by tempering and toughness may be deteriorated.

  In order to solve the above problem, Patent Document 3 proposes a tempering method in which the heating method is changed in the longitudinal direction of the steel sheet when tempering after accelerated cooling is performed by high-frequency induction heating. By this method, the strength of only the portion where the strength is too high, such as the longitudinal end portion of the steel plate, can be reduced, so that the strength variation can be greatly reduced.

  However, in order to obtain the effect sufficiently, it is necessary to accurately predict the strength distribution in the length direction of the steel plate after accelerated cooling, and to heat only the high strength part to an appropriate temperature. It has been difficult to stably obtain.

  As a method for manufacturing a steel sheet to which an induction heating device is applied, Patent Documents 4 and 5 disclose a method for manufacturing a steel sheet for sour line pipes that heats the surface of the steel sheet to a temperature higher than the inside after accelerated cooling.

  According to these methods, the hardness of the surface layer portion hardened by accelerated cooling can be reduced, and the hardness distribution in the plate thickness direction of the steel plate is leveled. The directional intensity variation remained unimproved.

Furthermore, when it becomes a thick material of 30 mm or more, it is necessary to increase the component in order to ensure the strength. However, the steel plate described in Patent Document 4 and Patent Document 5 has insufficient HAZ toughness due to insufficient chemical component studies. There was also a problem of deterioration.
JP 62-47426 A JP-A-4-358822 JP 2003-27136 A JP 2002-327212 A JP 2003-13138 A

  The present invention has been made in view of the above circumstances, and has a high strength and excellent base material, HAZ toughness and sour resistance performance, and a plate having excellent formability by reducing variation in strength within a steel plate. An object is to provide a steel sheet for high strength sour line pipe having a thickness of 30 mm or more, a method for producing the same, and a high strength sour line pipe manufactured using the steel sheet.

  As a result of detailed investigations on the cause of material variation in the steel sheet caused by accelerated cooling from the viewpoint of changes in the microstructure, the present inventors have obtained the following knowledge. As described above, the increase in strength at the longitudinal end of the steel sheet during accelerated cooling is due to overcooling, that is, due to the decrease in the cooling end temperature. Since the structure includes island-like martensite (MA), the hardness of the surface layer portion is significantly increased.

  FIG. 4 shows an example in which the plate thickness direction distribution after accelerated cooling of a steel plate (plate thickness: 32 mm) containing C: 0.04% and Mn: 1.2% is measured at the end and center in the longitudinal direction of the steel plate. . The steel sheet longitudinal direction end portion has a higher hardness of the surface layer portion than the center portion, and as a result, the total thickness strength of the steel plate also increases. FIG. 5 shows the result of erosion of the surface layer portion by two-stage etching and observation by SEM. The surface layer portion has a structure including island martensite. On the other hand, although the island-shaped martensite is seen in the central part of the plate thickness of the steel sheet, the volume fraction is small, and it can be said that the unevenness of the microstructure in the steel sheet is one of the causes of the steel sheet material variation.

  By suppressing the non-uniformity of the microstructure described above, specifically, the amount of island-like martensite in the steel sheet surface layer portion, it is possible to obtain a steel plate with small material variations. It is effective to decompose the island martensite generated in the surface layer. However, in the tempering by a general combustion furnace and the tempering by induction heating disclosed in Patent Document 2, the steel plate is heated up to the central portion in the thickness direction of the steel plate. As a result, the strength variation of the steel sheet is not sufficiently reduced.

  In order to solve this problem, when tempering the steel sheet after accelerated cooling, the tempering temperature of the steel sheet surface layer portion should be higher than that of the central portion in the plate thickness direction of the steel plate, and the heating temperature is set to the steel plate surface layer portion and the plate. By controlling to the optimum range in the central portion in the thickness direction, it is possible to obtain a steel plate having a small microstructure change in the thickness direction of the steel plate, thereby reducing material variations in the steel plate.

  In order to perform heating at different temperatures between the steel sheet surface layer and the inside as described above, it is effective to use high-frequency induction heating. FIG. 1 shows the same components as in FIG. 4, and the steel sheet plate that has been subjected to approximately the same rolling-accelerated cooling and then heated by induction heating to the maximum heating temperature of the steel sheet surface of 620 ° C. and the steel sheet cross-section average heating temperature of 470 ° C. Thickness direction hardness distribution. The microstructure of the steel sheet surface layer at this time is shown in FIG.

  The island-like martensite structure as seen in the steel sheet surface layer portion in the accelerated cooling state of FIG. 5 is not seen, and a uniform microstructure is obtained in the steel sheet surface layer portion and the central portion in the plate thickness direction. As shown in FIG. 1, the difference in hardness between the surface layer portion and the central portion in the plate thickness direction is small in both the longitudinal end portion and the longitudinal central portion of the steel plate. Moreover, by restricting the heating temperature at the central portion in the plate thickness direction of the steel plate, it is possible to suppress a decrease in strength of the whole steel plate and to reduce strength variation in the plate length direction.

  Also, not only the strength variation in the plate length direction of the steel plate, but also the hardness difference in the plate thickness direction is small, so the bending workability during cold forming is good, and the residual stress due to internal strain introduced by accelerated cooling However, since it is reduced by subsequent induction heating, the cold formability is good, and the dimensional accuracy after molding is greatly improved.

The present invention has been made based on the above findings and further studies.
1st invention is the mass%, C: 0.02-0.06%, Si: 0.5% or less, Mn: 0.5-1.5%, P: 0.01% or less, S: 0.001% or less, Al: 0.08% or less, Nb: 0.005-0.035%, Ti: 0.005-0.025%, Ca: 0.0010-0.0035%, Furthermore, Cu: 0.5% or less, Ni: 1% or less, Cr: 0.5% or less, Mo: 0.5% or less, V: 0.1% or less Steel, the balance being Fe and inevitable impurities are heated to 1000 to 1200 ° C. and hot-rolled, and then the cooling start temperature is equal to or higher than the steel sheet surface temperature (Ar 3 −10 ° C.) and cooling is stopped. Accelerated cooling is performed so that the temperature is 250 to 500 ° C. at the steel plate cross-sectional average temperature, and then the steel plate surface temperature is 550 by induction heating. 700 ° C., a process for producing a high strength sour linepipe steel plate thickness is more than 30mm, characterized in that heating to four hundred to five hundred eighty ° C. In the steel sheet cross-sectional mean temperature.

  The second invention is characterized in that the CP value represented by the following formula (1) is 1.0 or less and the Ceq value represented by the formula (2) is 0.3 or more. Is a method for producing a high-strength sour line pipe steel plate having a thickness of 30 mm or more.

  A third invention is a steel plate manufactured by the method according to the first or second invention, wherein the metal structure of the steel plate surface layer portion has a volume fraction of island martensite of 2% or less, and the balance Is a high strength sour line pipe steel plate having a plate thickness of 30 mm or more, characterized by being a bainite or a mixed structure of bainite and ferrite.

  A fourth invention is a high-strength sour line pipe manufactured by cold-forming the steel plate described in the third invention into a steel pipe shape and seam welding the butt portion.

  According to the present invention, the strength variation in the longitudinal direction of the steel sheet can be greatly reduced, and the hardness variation in the thickness direction can also be reduced. Therefore, excellent strength toughness, high material homogeneity and dimensional accuracy after cold forming Can be applied to steel plates for line pipes that are required. Furthermore, stable and excellent HIC resistance can be obtained.

In carrying out the invention, steel adjusted to the component composition range of the present invention to be described later is melted, and after continuous casting, the obtained steel slab is charged into a heating furnace or the like and heated to perform hot rolling. The rolling conditions may be arbitrarily selected as long as the rolling conditions of the present invention are satisfied, and the hot rolling end temperature may be not less than the lower limit (Ar 3 -10 ° C) of the cooling start temperature of accelerated cooling.

  After the hot rolling is completed, accelerated cooling is performed from a temperature equal to or higher than a predetermined cooling start temperature to a temperature within a predetermined cooling stop temperature range at a predetermined average cooling rate or higher under the cooling conditions of the present invention. After accelerated cooling, reheating is continued, or after further cooling from the cooling stop temperature in a cooling bed or the like, reheating is performed.

  Reheating after accelerated cooling is performed using an induction heating device. In particular, it is desirable to use a high-frequency induction heating device so that heating is concentrated on the surface layer of the steel sheet. In this way, when the surface layer part is heated by induction heating, a temperature distribution can be given such that the temperature of the surface layer part becomes higher than that of the central part of the steel sheet. By induction heating at a high frequency, the induction current can be concentrated on the surface layer of the steel sheet, and the current density can be increased compared to the inside.

  FIG. 3 is a diagram schematically showing a temperature change of the steel plate surface and the central portion when the thick steel plate is heated by the induction heating device. If an induction heating apparatus is used, since the current density of the steel plate surface layer portion is higher than the inside, the steel plate surface temperature is the highest and the temperature of the central portion is the lowest. When induction heating is started, the surface temperature rapidly rises, but when induction heating is stopped, the surface temperature rapidly decreases. At the same time, the temperature inside the steel sheet is slightly increased due to heat transfer from the surface layer portion, and the surface temperature and the inside temperature of the steel sheet are substantially equal.

  As for the temperature distribution in the plate thickness direction, the method using the gas combustion furnace of the prior art is uniform up to the plate thickness central portion of the steel plate, and the hardness of the surface layer portion is not deteriorated without deteriorating the material of the steel plate central portion as in the present invention. Could not be reduced.

  As for cooling after the reheating treatment, no deterioration of the DWTT characteristics is observed even with air cooling, and it is not necessary to specify a cooling rate. However, in a thick steel plate having a plate thickness exceeding about 35 mm, when the cooling rate becomes slow and there is a concern about toughness deterioration due to the coarsening of carbides, water cooling or mist cooling may be performed after the reheating treatment.

  The reasons for limiting the respective constituent requirements of the present invention will be described below.

1. About Chemical Components First, the reasons for limiting the chemical components contained in the steel sheet for high-strength sour line pipes of the present invention will be described. In addition, all component% means the mass%.

C: 0.02 to 0.06%
C is the most effective element for increasing the strength of the steel sheet produced by accelerated cooling. However, if it is less than 0.02%, sufficient strength cannot be secured, and if it exceeds 0.06%, toughness and HIC resistance are deteriorated. Accordingly, the C content is in the range of 0.02 to 0.06% Si: 0.5% or less Si is added for deoxidation, but if it exceeds 0.5%, the toughness and weldability are deteriorated. Therefore, the Si amount is set to a range of 0.5% or less.

Mn: 0.5 to 1.5%
Mn is added to improve the strength and toughness of the steel, but if it is less than 0.5%, the effect is not sufficient, and if it exceeds 1.5%, the weldability and HIC resistance deteriorate. Therefore, the amount of Mn is made 0.5 to 1.5%.

P: 0.01% or less P is an inevitable impurity element, and deteriorates weldability and HIC resistance. This tendency becomes remarkable when it exceeds 0.01%. Therefore, the P content is 0.01% or less.

S: 0.001% or less S is generally an MnS-based inclusion in steel, but its form is controlled from MnS-based to CaS-based inclusion by addition of Ca. However, if the S content is large, the amount of CaS inclusions also increases, and a high-strength material can be a starting point for cracking. This tendency becomes remarkable when the S amount exceeds 0.001%. Therefore, the S amount is 0.001% or less.

Al: 0.08% or less Al is added as a deoxidizer, but if it exceeds 0.08%, ductility is deteriorated due to a decrease in cleanliness. Therefore, the Al content is 0.08% or less.
Nb: 0.005 to 0.035%
Nb suppresses grain growth during rolling, and improves toughness by making fine grains. However, when the Nb content is less than 0.005%, the effect is not obtained, and when it exceeds 0.035%, the toughness of the weld heat affected zone deteriorates. Therefore, the Nb content is in the range of 0.005 to 0.035%.

Ti: 0.005-0.025%
Ti not only suppresses grain growth during slab heating by forming TiN, but also suppresses grain growth in the weld heat affected zone and improves toughness by making the base material and the weld heat affected zone finer. However, if the amount of Ti is less than 0.005%, the effect is not obtained, and if it exceeds 0.025%, the toughness is deteriorated. Therefore, the Ti amount is set in the range of 0.005 to 0.025%.

Ca: 0.001 to 0.0035%
Ca is an element effective for controlling the form of sulfide inclusions and improving ductility. However, if it is less than 0.001%, there is no effect, and even if added over 0.0035%, it is effective. Saturates, but rather deteriorates toughness due to reduced cleanliness. Therefore, the Ca content is in the range of 0.001 to 0.0035%.

  In the present invention, in addition to the chemical components described above, one or more selected from the following elements are added as selective elements.

Cu: 0.5% or less Cu is an element effective for improving toughness and increasing strength, but if added over 0.5%, weldability deteriorates. Therefore, when adding Cu, it is 0.5% or less.

Ni: 1% or less Ni is an element effective for improving toughness and increasing strength, but if it exceeds 1%, weldability deteriorates. Therefore, when adding Ni, it is 1.0% or less.

Cr: 0.5% or less Cr is an element effective for increasing the strength by improving the hardenability, but if added over 0.5%, the weldability is deteriorated. Therefore, when adding Cr, it is 0.5% or less.

Mo: 0.5% or less Mo is an element effective for improving toughness and increasing strength, but if added over 0.5%, weldability deteriorates. Therefore, when adding Mo, it is 0.5% or less.

V: 0.1% or less V is an element that increases strength without deteriorating toughness, but if added over 0.1%, weldability is significantly impaired. Therefore, when V is added, the content is made 0.1% or less.
The balance of the steel of the present invention is substantially Fe, and elements other than the above and inevitable impurities can be contained unless the effects of the present invention are impaired.

  In the present invention, it is further desirable that the CP value represented by the following formula (1) is 1.0 or less and the Ceq value represented by the following formula (2) is 0.3 or more. Here, C (%), Mn (%), Cr (%), Mo (%), V (%), Cu (%), Ni (%), and P (%) are the contents of each element. (Mass%).

  The CP value is an equation devised to estimate the material of the center segregation part from the content of each alloy element. The higher the CP value, the higher the concentration of the center segregation part and the higher the hardness of the center segregation part. . By setting the CP value to 1.0 or less, the hardness of the central segregation portion can be reduced, and cracks in the HIC test can be suppressed. The lower the CP value, the lower the hardness of the center segregation part. Therefore, when higher HIC resistance is required, the upper limit is desirably set to 0.95.

  The Ceq value is a hardenability index of steel, and the higher the Ceq value, the higher the strength of the steel material. The present invention aims at improving the HIC performance of a thick sour line pipe having a thickness of 30 mm or more. In order to obtain sufficient strength with a thick material, the Ceq value is desirably 0.30 or more.

2. Manufacturing conditions The present invention is a manufacturing method in which a steel slab containing the above chemical components is heated and hot-rolled, and then subjected to accelerated cooling, followed by tempering by induction heating. Below, the reason for limitation of the manufacturing conditions of a steel plate is demonstrated.

Slab heating temperature: 1000-1200 ° C
When the slab heating temperature is less than 1000 ° C., sufficient strength cannot be obtained, and when it exceeds 1200 ° C., toughness and DWTT characteristics are deteriorated. Therefore, the slab heating temperature is in the range of 1000 to 1200 ° C.

  In the hot rolling process, in order to obtain high base metal toughness, the lower the rolling end temperature is better, but on the other hand, the rolling efficiency is lowered, so the rolling end temperature is arbitrary in view of the required base material toughness and rolling efficiency. Can be set. In order to obtain high base metal toughness, it is desirable that the rolling reduction in the non-recrystallization temperature range be 60% or more.

  After hot rolling, accelerated cooling is performed under the following conditions.

Steel sheet surface temperature at the start of cooling: (Ar 3 −10 ° C.) or more Accelerated cooling is performed after hot rolling. If the steel sheet surface temperature at the start of cooling is low, the amount of ferrite generated before accelerated cooling increases, and Ar 3 When the temperature drop from the transformation point exceeds 10 ° C., the HIC resistance deteriorates. Therefore, the steel plate surface temperature at the start of cooling is set to (Ar 3 -10 ° C) or higher.
Here, the Ar 3 temperature is given by the following formula (3) from the steel components.

Average temperature of steel plate cross section when cooling is stopped: 250 to 550 ° C
Accelerated cooling is an important process for obtaining high strength by bainite transformation. However, if the average cross-sectional temperature of the steel sheet when cooling is stopped exceeds 550 ° C., the bainite transformation is incomplete and sufficient strength cannot be obtained. In addition, when the average temperature of the cross section of the steel sheet when cooling is stopped is less than 250 ° C., not only the hardness of the surface layer portion of the steel sheet becomes too high, but also the steel sheet tends to be distorted and formability deteriorates. Therefore, the steel plate cross-sectional average temperature when cooling is stopped is set to 250 to 550 ° C.

  The cooling rate in the accelerated cooling is preferably a cooling rate of 5 ° C./s or more in order to stably obtain a sufficient strength.

  Following accelerated cooling, tempering by induction heating is performed. Here, the use of the induction heating device enables rapid heating, and furthermore, the heating temperature of the steel sheet, which is an important requirement of the present invention, can be changed between the steel sheet surface layer part and the plate thickness central part. Because. Below, the reason for limitation of the heating conditions by induction heating is demonstrated.

Steel plate surface temperature: 550 to 700 ° C
By heating the steel plate surface layer portion, the island martensite generated by accelerated cooling is decomposed, and the hardness of the surface layer portion is reduced. However, if the surface temperature is less than 550 ° C., the island-like martensite is not sufficiently decomposed, so that the hardness is not sufficiently lowered. Much. Therefore, the steel sheet surface temperature in induction heating is set to a range of 550 to 700 ° C. Moreover, since the surface layer part is heated by induction heating and the inside of the steel sheet is heated by heat conduction, the temperature of the surface layer part becomes higher than the inside of the steel sheet, but the rise of the steel sheet cross-section average heating temperature is suppressed, and the hardness of the surface layer part In order to effectively reduce the temperature, it is desirable that the surface temperature of the steel sheet by induction heating is higher than the average heating temperature of the steel sheet cross section by 100 ° C. or more.

Steel sheet cross-section average heating temperature: 400-580 ° C
By induction heating after accelerated cooling, the strength variation inside the steel sheet can be greatly reduced. However, if the heating temperature at the center of the steel sheet is less than 400 ° C., the variation is insufficiently reduced, and if it exceeds 580 ° C., not only does the strength decrease due to tempering, but also the DWTT performance deteriorates. Therefore, the steel sheet cross-section average heating temperature by induction heating is set to a range of 400 to 580 ° C. In order to further reduce the variation in strength, it is desirable that the average heating temperature of the steel sheet cross section by induction heating is in the range of 450 to 580 ° C.

  In addition, steel plate cross-section average heating temperature is the temperature averaged in the cross section, when there exists temperature distribution in the steel plate thickness direction. However, the difference between the steel plate surface temperature and the steel plate center temperature generated immediately after accelerated cooling or induction heating becomes a substantially uniform temperature distribution within the steel plate after a while due to heat conduction. good.

3. Regarding the metal structure In the present invention, the hardness of the steel sheet surface layer portion is reduced by the heat treatment after accelerated cooling, and the hardness distribution in the plate thickness direction is smoothed, but the metal structure of the steel sheet surface layer portion is defined as follows. .

Volume fraction of island martensite in the steel sheet surface layer portion: 2% or less Island martensite (MA) is a structure generated by accelerated cooling, and the hardness increases greatly when island martensite is generated. However, if the volume fraction is less than 2%, the difference in hardness from the central portion of the steel sheet is sufficiently small, so the upper limit of the volume fraction of island martensite is set to 2%. The balance is bainite or a mixed structure of bainite and ferrite.

  The present invention is a technique that can be applied to a steel sheet having a plate thickness of 30 mm or more and can reduce the hardness of the surface layer portion of the steel sheet without deteriorating the strength and DWTT performance. In accelerated cooling of a steel plate having a plate thickness of 30 mm or more, the temperature of the steel plate surface is lower than the temperature inside the steel plate, and the surface temperature of the steel plate needs to be sufficiently low in order to obtain a predetermined steel plate cross-sectional average temperature. At this time, since the amount of island-shaped martensite generated in the steel plate surface layer portion increases, the hardness of the steel plate surface layer portion increases. Therefore, the heat treatment by induction heating of the present invention is important. However, in accelerated cooling of a relatively thin steel plate having a thickness of less than 30 mm, the temperature drop of the steel plate surface layer portion is small, and the increase in the hardness of the steel plate surface layer portion is not large, so it is not necessary to apply the present invention. Therefore, the plate thickness of the steel plate to which the present invention is applied is set to 30 mm or more.

4). About the manufacturing method of a steel pipe The 4th invention of this invention is a sour-resistant pipe manufactured using said steel plate, and demonstrates the manufacturing method of a steel pipe below.

  As a method for forming a steel pipe, a steel sheet is formed into a steel pipe shape by cold forming such as UOE process or press bend. After that, the butt joint is seam welded. Any welding method can be used as long as sufficient joint strength and joint toughness can be obtained, but submerged arc welding is used from the viewpoint of excellent welding quality and production efficiency. It is preferable. After welding the butt, pipe expansion is performed to remove the residual welding stress and improve the roundness of the steel pipe. The expansion ratio at this time is preferably set to 0.5 to 1.5% as a condition for obtaining a predetermined roundness of the steel pipe and removing the residual stress.

  Steels (steel types A to J) having chemical components shown in Table 1 were made into slabs by a continuous casting method, and thick steel plates (No. 1 to 21) having a plate thickness of 30 to 38 mm were produced using the slabs.

  The heated slab was rolled by hot rolling. The length of the steel plate after hot rolling was 25 m. Immediately after hot rolling, cooling was performed using a water-cooled accelerated cooling facility, and reheating was performed using an induction heating furnace installed on the same line as the accelerated cooling facility. Some steel plates were not reheated for comparison. Table 2 shows the production conditions of each steel plate (No. 1 to 21).

  As for the tensile properties of the steel sheet produced as described above, a tensile test was performed using a full thickness test piece in the rolling direction as a tensile test piece, and the tensile strength was measured. The tensile strength of 530 MPa or more was determined as the strength required for the present invention. Here, in order to confirm the variation in strength in the steel sheet, tensile test pieces were taken from the longitudinal end and the longitudinal center of the steel sheet, and the difference was used as the strength variation.

  Furthermore, about the steel plate longitudinal direction center part, the observation and hardness of the metal structure of the steel plate were measured. The structure of the steel sheet surface layer part was subjected to electrolytic etching after two-stage etching (two-stage etching), and the area fraction of island martensite (MA) was measured.

  In the hardness test, the hardness of the steel sheet surface layer part (1 mm below the surface) and the plate thickness center part was measured using a Vickers hardness tester with a load of 10 kg. And the difference was made into the variation in hardness. Hardness variation was 25 or less as examples of the present invention.

  For the weld heat affected zone (HAZ) toughness, Charpy tests were conducted at various temperatures using test pieces to which a thermal history corresponding to a heat input of 40 kJ / cm was applied by a reproducible thermal cycle apparatus. The temperature at which the brittle fracture surface ratio was 50% was determined as the fracture surface transition temperature (vTrs).

Moreover, about these steel plates, HIC resistance and DWTT characteristic were investigated. The HIC resistance was examined by an HIC test conducted in 5% NaCl + 0.5% CH 3 COOH aqueous solution (normal NACE solution) saturated with hydrogen sulfide having a pH of about 3. In the HIC test, the length of the crack was measured for three cross sections (cut at equal intervals) of the test piece, and the average value of the crack length with respect to the width of the test piece was measured for all cross sections. ). And the case where the crack length ratio was 10% or less was taken as an example of the present invention. The DWTT property was evaluated at a temperature (85% SATT) at which the ductile fracture surface ratio was 85% in a DWTT test (Drop Weight Tear Test) using an API-standard press notch specimen reduced to 19 mm. 85% SATT was set to -20 ° C. or less as an example of the present invention.

  In Table 2, Nos. 1 to 7 and Nos. As for 18-21, as for all, a chemical component, a manufacturing method, and a microstructure are in the range of the present invention, the tensile strength is high strength of 530 MPa or more, and the strength variation in a steel plate is as small as 20 MPa or less. Furthermore, since the variation in hardness in the thickness direction is small, it can be said that the bending workability during cold forming is very good. The weld heat-affected zone toughness and DWTT characteristics were also good, and the HIC resistance was good at a crack length ratio of 10% or less. In addition, the CP value and the Ceq value are the preferred ranges of the present invention. Nos. 1 to 7, 18 and 19 showed particularly high strength and excellent HIC resistance.

  On the other hand, in Nos. 8 to 14, the chemical components are within the scope of the present invention and the welded portion toughness is excellent. Therefore, the resistance to HIC is inferior, and the amount of island-like martensite (MA) in the surface layer portion of the steel sheet exceeds the range of the present invention, resulting in large variations in strength and hardness. Nos. 15 to 17 had chemical components outside the scope of the present invention, so that sufficient strength could not be obtained, or welding heat affected zone toughness or HIC resistance was inferior.

  Next, No. 1 shown in Table 2 was obtained. Steel pipes were manufactured by the UOE process using 1, 7, 10, 12, 16, 18 steel plates. The butt portion was welded by four-electrode submerged arc welding with one pass on each of the inner and outer surfaces. And 1% pipe expansion was given by the outer periphery change of the steel pipe after welding. The manufactured steel pipe was subjected to a full thickness tensile test, a hardness test, a DWTT test, and an HIC test in the same manner as the material test of the steel sheet. Further, the HAZ toughness was evaluated by the absorbed energy at a test temperature of −20 ° C. by performing a Charpy test in which a notch was introduced into the heat-affected zone of the outer surface weld. The DWTT test was conducted at −17 ° C., and the ductile fracture surface ratio (SA) at this time was evaluated.

  Table 3 shows the material test results of the steel pipe.

  P1 to P3 are steel pipes manufactured using a steel plate within the scope of the present invention, and are excellent in strength, surface layer hardness, HAZ toughness, DWTT characteristics, and HIC resistance. On the other hand, P4 to P6 are steel pipes manufactured using a steel sheet outside the scope of the present invention, and the HIC resistance is inferior or the surface hardness is high.

  According to the present invention, the tensile strength is not less than 530 MPa, high weld toughness, HIC resistance and DWTT properties, and the strength variation in the longitudinal direction of the steel sheet can be greatly reduced, and the hardness in the thickness direction can be further reduced. Therefore, a steel sheet having excellent cold formability can be obtained. For this reason, it can be applied to line pipe applications that require excellent strength toughness, high material homogeneity, and dimensional accuracy after cold forming.

It is a figure explaining the thickness direction hardness distribution after induction heating. It is a SEM observation photograph of the steel plate surface layer part after induction heating. It is a schematic diagram explaining the temperature history of the steel plate surface at the time of induction heating, and a steel plate center part. It is a figure explaining the thickness direction hardness distribution after accelerated cooling. It is a SEM observation photograph of the steel sheet surface layer part after accelerated cooling.

Claims (4)

  1. In mass%, C: 0.02 to 0.06%, Si: 0.5% or less, Mn: 0.5 to 1.5%, P: 0.01% or less, S: 0.001% or less, Al: 0.08% or less, Nb: 0.005 to 0.035%, Ti: 0.005 to 0.025%, Ca: 0.0010 to 0.0035%, and Cu: 0.005%. 5% or less, Ni: 1% or less, Cr: 0.5% or less, Mo: 0.5% or less, V: 0.1% or less After steel comprising Fe and inevitable impurities is heated to 1000 to 1200 ° C. and hot-rolled, the cooling start temperature is equal to or higher than the steel sheet surface temperature (Ar 3 −10 ° C.), and the cooling stop temperature is the steel sheet cross-sectional average temperature. At 250 to 500 ° C., followed by induction heating at a steel sheet surface temperature of 550 to 700 ° C., steel Method of producing a high strength sour linepipe steel plate thickness is more than 30mm, characterized in that heating to 400-580 ° C. in cross-section average temperature.
  2. The plate thickness according to claim 1, wherein the CP value represented by the following formula (1) is 1.0 or less, and the Ceq value represented by the formula (2) is 0.3 or more. The manufacturing method of the steel plate for the above high-strength sour line pipes.
  3.   A steel sheet produced by the method according to claim 1 or 2, wherein the surface area of the steel sheet has an island-like martensite volume fraction of 2% or less, and the balance is bainite or a mixture of bainite and ferrite. A steel sheet for high strength sour line pipes having a thickness of 30 mm or more, characterized by being a structure.
  4.   A high-strength sour-line pipe produced by cold-forming the steel plate according to claim 3 into a steel pipe shape and seam welding the butt portion.
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US20120305122A1 (en) 2009-11-25 2012-12-06 Nobuyuki Ishikawa Welded steel pipe for linepipe having high compressive strength and high fracture toughness and manufacturing method thereof
KR101511614B1 (en) * 2009-11-25 2015-04-13 제이에프이 스틸 가부시키가이샤 Method for manufacturing welded steel pipe for linepipe having high compressive strength and excellent sour gas resistance
CN102666898A (en) * 2009-11-25 2012-09-12 杰富意钢铁株式会社 Welded steel pipe for linepipe with superior compressive strength, and process for producing same
JP5605136B2 (en) * 2010-09-30 2014-10-15 Jfeスチール株式会社 High strength steel plate with excellent material uniformity in steel plate and method for producing the same
JP5672916B2 (en) * 2010-09-30 2015-02-18 Jfeスチール株式会社 High-strength steel sheet for sour line pipes, method for producing the same, and high-strength steel pipe using high-strength steel sheets for sour line pipes
JP5751012B2 (en) * 2011-05-24 2015-07-22 Jfeスチール株式会社 Manufacturing method of high-strength line pipe with excellent crush resistance and sour resistance
JP5803270B2 (en) * 2011-05-24 2015-11-04 Jfeスチール株式会社 High strength sour line pipe excellent in crush resistance and manufacturing method thereof
JP5751013B2 (en) * 2011-05-24 2015-07-22 Jfeスチール株式会社 Manufacturing method of high-strength line pipe with excellent crush resistance and sour resistance
JP5796351B2 (en) * 2011-05-24 2015-10-21 Jfeスチール株式会社 High strength sour line pipe excellent in crush resistance and manufacturing method thereof
KR101299361B1 (en) * 2011-06-28 2013-08-22 현대제철 주식회사 Steel and manufacturing method of steel pipe using the steel
JP5900303B2 (en) * 2011-12-09 2016-04-06 Jfeスチール株式会社 High-strength steel sheet for sour-resistant pipes with excellent material uniformity in the steel sheet and its manufacturing method
JP5991174B2 (en) * 2011-12-09 2016-09-14 Jfeスチール株式会社 High-strength steel sheet for sour-resistant pipes with excellent material uniformity in the steel sheet and its manufacturing method
JP5991175B2 (en) * 2011-12-09 2016-09-14 Jfeスチール株式会社 High-strength steel sheet for line pipes with excellent material uniformity in the steel sheet and its manufacturing method
WO2013190750A1 (en) 2012-06-18 2013-12-27 Jfeスチール株式会社 Thick, high-strength, sour-resistant line pipe and method for producing same
CN104428437B (en) 2012-07-09 2017-03-08 杰富意钢铁株式会社 Thick section and high strength acid resistance line pipe and its manufacture method
JP5928405B2 (en) * 2013-05-09 2016-06-01 Jfeスチール株式会社 Tempered steel sheet excellent in resistance to hydrogen-induced cracking and method for producing the same
JP6193206B2 (en) 2013-12-11 2017-09-06 株式会社神戸製鋼所 Steel plate and line pipe steel pipe with excellent sour resistance, HAZ toughness and HAZ hardness
CN105861937A (en) * 2016-03-31 2016-08-17 首钢总公司 Low-temperature pipeline steel used for LNG transmission trunk line and preparation method thereof

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