JP2010202949A - Method for manufacturing steel material for line-pipe - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a method for manufacturing a steel material for line pipe, having ≥760 MPa tensile strength and uniform extension after strain-ageing. <P>SOLUTION: A steel strip or steel ingot having chemical-composition containing respective prescribed contents of C, Si, Mn, Cu, Ni, Mo. Nb, Ti and Al and the balance Fe with impurities of P, S, N and O in the respective prescribed contents or lower, is used, and heating, rolling and accelerated cooling are performed to the steel strip or steel ingot under the condition that P value obtained from a formula: P=24+66C+2Si-2Mo-0.005T<SB>h</SB>-0.02T<SB>r</SB>-0.002T<SB>c</SB>is ≥5.9, and that the temperature of accelerated cooling stop is ≤400°C. Wherein, the symbols of the elements (C, Si and Mo) represent respective element contents (mass%) in the steel, T<SB>h</SB>represents heating temperature (°C) before rolling, T<SB>r</SB>represents rolling-finish temperature (°C), and T<SB>c</SB>represents the accelerated cooling stop temperature (°C). <P>COPYRIGHT: (C)2010,JPO&INPIT

Description

  The present invention relates to a method for manufacturing a steel material for line pipes, and more particularly to a method for manufacturing a steel material for line pipes having a tensile strength of 760 MPa or more and excellent strain aging characteristics.

  When transporting a large amount of natural gas or crude oil, a large-diameter line pipe is used. Steel for line pipes is required to have high strength and toughness, and SBD (Strain-Based Design) with high deformation performance to prevent damage to the pipeline due to ground movement during earthquakes, thawing / freezing of frozen soil, etc. ) Corresponding steel is desired. In particular, the base material is required to be improved in deformation performance and strain aging characteristics in order to prevent local buckling. The deformation performance is low YR (yield ratio) and high U.D. It is improved when it is El (uniform elongation). Deformation performance deteriorates due to strain aging due to heating during pipe forming and coating. By the way, it is generally said that the higher the strength, the more difficult it is to secure high deformation performance after strain aging.

  In response to such demands, a technique for improving the strain aging resistance of steel materials by controlling the chemical composition or production conditions is disclosed. For example, Patent Document 1 discloses “a high-strength steel material excellent in strain aging characteristics and a manufacturing method thereof”. Patent Document 2 discloses “a steel pipe for high-strength line pipe excellent in strain aging resistance, a steel sheet for high-strength line pipe, and a manufacturing method thereof”.

JP 2002-220634 A JP 2007-314828 A

  According to the manufacturing method disclosed in Patent Document 1, it is said that good strain aging characteristics can be obtained, but this method is only intended for steel materials having a tensile strength of 600 MPa or more. Therefore, the steel material obtained by this method may not have a strength of 760 MPa or more and good uniform elongation after strain aging.

  The manufacturing method disclosed in Patent Document 2 is intended to reduce the change in yield strength before and after strain aging, and is not intended to improve uniform elongation. For this reason, the steel plate obtained by the manufacturing method disclosed in Patent Document 2 may not have good uniform elongation after strain aging.

  Therefore, an object of the present invention is to provide a method for producing a steel material for a line pipe that is suitable as a material for a line pipe, particularly having a tensile strength of 760 MPa or more after strain aging and excellent in uniform elongation.

  In order to solve the above problems, the present inventors have made various studies. As a result, the knowledge shown in the following (a) to (e) was obtained.

  (A) Good deformation performance before and after strain aging, that is, low YR and high U.V. In order to obtain El, in the chemical composition of steel, it is better that the C content and the Si content are larger and the Mo content is smaller.

(B) Good deformation performance before and after strain aging, that is, low YR and high U.V. To obtain El, the heating temperature T _h before _rolling, finish rolling temperature T _r and the accelerated cooling stop temperature T _c are all lower is better.

(C) In addition to optimizing the chemical composition of the steel, if the heating temperature T _h before rolling, rolling finishing temperature T _r , accelerated cooling stop temperature T _c, etc. are appropriately controlled, a high tensile strength of 760 MPa or more It is possible to have a large uniform elongation.

(D) As shown in FIG. El (product of strength and uniform elongation) has a correlation with the P value shown in the following equation (1).
P = 24 + 66C + 2Si- 2Mo-0.005T h -0.02T r -0.002T c (1)
However, (1) the elements in the formula symbols (C, Si and Mo) are in the steel the content of respective elements (mass%), _{T h,} the heating temperature before rolling (° C.), _{T r} is the rolling Finishing temperature (° C.) and T _c mean accelerated cooling stop temperature (° C.), respectively.

  (E) By adjusting the chemical composition and production conditions so that the P value is 5.9 or more and the accelerated cooling stop temperature is 400 ° C. or less, TS × U. The value of El can be 6000 or more.

  This invention is completed based on said knowledge, The summary exists in the manufacturing method of the steel materials for line pipes whose tensile strength shown to following (1)-(3) is 760 Mpa or more.

(1) By mass%, C: more than 0.07 to 0.14%, Si: 0.2 to 0.9%, Mn: 1.0 to 3.0%, Cu: 0.05 to 1.0 %, Ni: 0.05-1.5%, Mo: 0.04-0.20%, Nb: 0.005-0.08%, Ti: 0.005-0.04% and sol. Al: 0.005 to 0.100% is contained, the balance is made of Fe and impurities, and P, S, N and O as impurities are respectively P: 0.02% or less, S: 0.005% or less, Using a steel slab or steel ingot having a chemical composition of N: 0.010% or less and O: 0.005% or less, the P value obtained from the formula (1) is 5.9 or more and accelerated cooling is stopped. A method for producing a steel product for a line pipe having a tensile strength of 760 MPa or more, in which heating, rolling and accelerated cooling are performed under conditions where the temperature is 400 ° C. or lower.
P = 24 + 66C + 2Si- 2Mo-0.005T h -0.02T r -0.002T c (1)
However, (1) the elements in the formula symbols (C, Si and Mo) are in the steel the content of respective elements (mass%), _{T h,} the heating temperature before rolling (° C.), _{T r} is the rolling Finishing temperature (° C.) and T _c mean accelerated cooling stop temperature (° C.), respectively.

  (2) The steel slab or the steel ingot further contains, in mass%, one or more selected from Cr: 1.0% or less, V: 0.5% or less, and B: 0.01% or less ( 1) The manufacturing method of the steel materials for line pipes.

  (3) The steel slab or the steel ingot further contains 1% or more selected from Ca: 0.01% or less, REM: 0.02% or less, and Mg: 0.008% or less in mass%. (1) The manufacturing method of the steel material for line pipes of (2).

  The heating temperature before rolling refers to the temperature of the material to be rolled on the heating furnace exit side. The rolling finishing temperature refers to the temperature of the material to be rolled when biting into the roll in the final rolling pass. The accelerated cooling stop temperature means the maximum temperature reached after reheating of the material to be rolled. The temperature of these materials to be rolled means the average temperature in the surface portion.

  According to the method for manufacturing a steel product for a line pipe of the present invention, a line pipe material excellent in deformation performance after strain aging can be manufactured in addition to a high strength of 760 MPa or more before and after strain aging.

Ingredient / Manufacturing Condition Parameter P Value and TS × U. Diagram showing the relationship with El

  Hereinafter, each requirement of the present invention will be described in detail. In addition, “%” of the content of each element in the chemical composition means “mass%”.

(A) Chemical composition C: more than 0.07% and 0.14% or less C is an element necessary for increasing the strength of steel. In order to stably obtain a tensile strength of 760 MPa or more, C needs to be a content exceeding 0.07%. On the other hand, if the C content becomes too large, weld cracks are likely to occur. Therefore, the C content is more than 0.07% and 0.14% or less. The C content is preferably more than 0.08%. Moreover, the preferable upper limit of C is 0.12%.

Si: 0.2-0.9%
Si has good deformation performance before and after strain aging, that is, low YR and high U.V. Effective for obtaining El. In order to reliably obtain these effects, Si is contained in an amount of 0.2% or more. However, if the Si content is too large, the toughness of the base metal and the weld heat affected zone (hereinafter referred to as “HAZ”) is significantly deteriorated. Therefore, the Si content is set to 0.2 to 0.9%. The Si content is preferably more than 0.3%, and more preferably more than 0.5%. Moreover, the upper limit with preferable Si content is 0.8%, and a more preferable upper limit is 0.75%.

Mn: 1.0-3.0%
Mn has the effect | action which raises the intensity | strength of steel. In order to obtain this effect sufficiently, Mn is contained at 1.0% or more. On the other hand, if the content is excessive, weld cracks are likely to occur. In addition, when the Mn content is large, good deformation characteristics aimed by the present invention, that is, low YR, high U.D. It becomes difficult to obtain El. Therefore, the Mn content is set to 1.0 to 3.0%. The minimum with preferable Mn content is 1.2%, and a more preferable minimum is 1.5%. Moreover, the upper limit with preferable Mn content is 2.5%, and a more preferable upper limit is 2.0%.

Cu: 0.05 to 1.0%
Cu has the effect of improving the strength of the steel material, so 0.05% or more is contained. However, if the content is large, the surface properties and toughness of the steel material are significantly deteriorated. Therefore, the Cu content is set to 0.05 to 1.0%. A preferable lower limit of the Cu content is 0.1%. Moreover, a preferable upper limit is 0.6%. Furthermore, the lower limit of the Cu content is preferably 0.2%, and the upper limit is more preferably 0.5%.

Ni: 0.05 to 1.5%
Ni has the effect | action which improves the intensity | strength of steel materials, and also has the effect | action which improves toughness. In order to exhibit these effects, it is necessary to contain Ni 0.05% or more. However, if the Ni content exceeds 1.5%, an effect commensurate with the cost increase cannot be obtained. Therefore, the Ni content is set to 0.05 to 1.5%. A preferable lower limit of the Ni content is 0.1%. Moreover, a preferable upper limit is 1.0%. Further, the lower limit of the Ni content is preferably 0.2%, and the upper limit is more preferably 0.6%.

Mo: 0.04 to 0.20%
Since Mo has an effect of improving the strength of the steel material, it is necessary to contain 0.04% or more. However, if the content is excessive, the increase in YS due to strain aging increases, and the deformation characteristics are impaired. Moreover, HAZ toughness deterioration and weld cracking are likely to occur. Therefore, the Mo content is set to 0.04 to 0.20%. A preferable lower limit of the Mo content is 0.05%. Moreover, a preferable upper limit is 0.15%. Furthermore, the lower limit of the Mo content is preferably 0.07%, more preferably 0.13%.

Nb: 0.005 to 0.08%
Nb has the effect of improving the strength of the steel material, and also has the effect of increasing the base material toughness by combining with appropriate rolling conditions. For this reason, Nb needs to be contained by 0.005% or more. However, if the content is too large, the toughness of the base material and the HAZ deteriorates. Therefore, the Nb content is set to 0.005 to 0.08%. A preferred lower limit is 0.01%. Moreover, a preferable upper limit is 0.06%. Furthermore, the Nb content is preferably 0.02% at the lower limit, and more preferably 0.05% at the upper limit.

Ti: 0.005-0.04%
Ti forms precipitates (TiN) with N to improve the toughness of HAZ, so it is necessary to contain Ti by 0.005% or more. However, when the content exceeds 0.04%, the base material and the HAZ toughness deteriorate. Therefore, the content of Ti is set to 0.005 to 0.04%. A preferred lower limit is 0.01%. A preferable upper limit is 0.03%. Also, the increase in YR after strain aging and the U.S. In order to suppress the decrease in El, the ratio of Ti to N content (Ti / N) is preferably 4.0 or more.

sol. Al: 0.005 to 0.100%
Al is an element having a deoxidizing action. Since it is effective in improving El, sol. Al (“acid-soluble Al”) is contained in an amount of 0.005% or more. However, sol. If the Al content becomes too large, the toughness of the HAZ will deteriorate. Therefore, sol. The Al content was 0.005 to 0.100%. Note that sol. More preferably, the lower limit of the Al content is 0.010% and the upper limit is 0.060%.

  Moreover, although the main component of the balance of the steel slab or steel ingot used for the production method of the present invention is Fe, the properties of the steel may be deteriorated due to inclusion of other components due to various factors in the production process. There is sex. Therefore, in order to ensure the targeted good performance, the content of the following components contained in the impurities is particularly controlled. An impurity means the component mixed by raw materials and other factors, such as an ore and a scrap, when manufacturing steel materials industrially.

P: 0.02% or less P is an element that causes deterioration of toughness, and its content increases. In particular, when it exceeds 0.02%, the deterioration of toughness tends to be remarkable. Therefore, the content of P is set to 0.02% or less. In addition, it is better that the content of P is small, and it is preferably 0.01% or less.

S: 0.005% or less S increases the content of inclusions that are harmful to ductility or toughness. In particular, when it exceeds 0.005%, inclusions increase and the ductility and the toughness deteriorate significantly. Therefore, the content of S is set to 0.005% or less. In addition, it is better that the content of S is small, and it is preferable that the content is 0.003% or less.

N: 0.010% or less N increases the toughness of HAZ as the content increases. In particular, if it exceeds 0.010%, the HAZ toughness is significantly deteriorated. Therefore, the N content is set to 0.010% or less. The N content is preferably 0.009% or less. More preferably, it is 0.005% or less.

O: 0.005% or less O (oxygen) may be effective for the formation of oxides that form ferrite nuclei if the content is very small, but if the content is high, the base material toughness and ductility are adversely affected. Effect. Therefore, the content of O is set to 0.005% or less. The O content is more preferably 0.002% or less.

  The steel slab or the steel ingot used in the production method of the present invention may contain one or more selected from the following elements as necessary.

Cr: 1.0% or less Since Cr is an element effective for improving the strength of a steel material, it may be contained. However, if the Cr content is excessive, weld cracks are likely to occur. Therefore, when it contains Cr, the content shall be 1.0% or less. The Cr content is preferably 0.5% or less. The above effect becomes remarkable when Cr is contained in an amount of 0.01% or more. The minimum with preferable content of Cr is 0.02%.

V: 0.5% or less V is an element effective for improving the strength of a steel material, so may be contained. However, when the content is excessive, ductility and toughness may be deteriorated. Therefore, when V is contained, the content is set to 0.5% or less. The above effect becomes remarkable when the content is 0.001% or more. The minimum with preferable V content is 0.005%.

B: 0.01% or less B is an element effective for improving the strength of a steel material, and therefore may be contained. However, when the content is excessive, ductility and toughness may be deteriorated. Therefore, when B is contained, the content is set to 0.01% or less. The B content is preferably less than 0.002%. The above effect becomes remarkable when B is contained by 0.0001% or more. A preferable lower limit of the B content is 0.0004%.

Ca: 0.01% or less,
REM: 0.02% or less Since Ca and REM are effective elements for controlling the form of sulfide (particularly MnS) and improving low-temperature toughness, they may be contained. However, if the content is excessive, inclusions containing Ca and REM may be coarsened and clustered, which may impair the cleanliness of steel and adversely affect weldability. For this reason, it is preferable that the upper limit of Ca amount and REM amount be 0.01% or less and 0.02% or less, respectively. In particular, from the viewpoint of weldability, the upper limit of the Ca content is preferably 0.006% or less. In order to obtain the above effects, it is preferable to contain Ca by 0.0005% or more and REM by 0.001% or more. Note that REM is a general term for a total of 17 elements of Sc, Y, and lanthanoid, and can contain one or more selected from these elements. The content of REM means the total amount of the above elements.

Mg: 0.008% or less Mg forms an finely dispersed oxide, and suppresses the coarsening of the particle size of the HAZ and exhibits the effect of improving the low temperature toughness. In order to obtain this effect, Mg may be contained. However, when Mg is contained in excess of 0.008%, a coarse oxide may be generated and toughness may be deteriorated. For this reason, when it contains Mg, the content shall be 0.008% or less. In order to acquire said effect, it is preferable to contain 0.0005% or more of Mg.

(B) Manufacturing conditions Even if the chemical composition is as described above, the tensile strength and uniform elongation after strain aging may not be ensured. Therefore, it is necessary to satisfy the condition that the value of P obtained from the following equation (1) is 5.9 or more.
P = 24 + 66C + 2Si- 2Mo-0.005T h -0.02T r -0.002T c (1)
However, (1) the elements in the formula symbols (C, Si and Mo) are in the steel the content of respective elements (mass%), _{T h,} the heating temperature before rolling (° C.), _{T r} is the rolling Finishing temperature (° C.) and T _c mean accelerated cooling stop temperature (° C.), respectively.

  That is, when the P value is less than 5.9, TS × U. It becomes difficult to obtain a good characteristic that the value of El is 6000 or more. TS × U. In order to further improve the value of El (6800 or more), it is preferable to set the P value to 8.5 or more.

  Accelerated cooling after rolling (also simply referred to as “cooling”) is good TS × U. In order to ensure the value of El, the cooling stop temperature needs to be 400 ° C. or lower. Moreover, it becomes easy to obtain low YR by setting the cooling stop temperature to 400 ° C. or lower.

  The manufacturing conditions may satisfy the above conditions, but more preferable conditions in each step will be described below.

  The heating temperature before rolling is preferably 850 ° C. or higher. By heating the slab to such a temperature, hot rolling of the steel material becomes easy. The heating temperature before rolling is more preferably 950 ° C. or higher. However, if the heating temperature of the slab is too high, the P value shown in the formula (1) becomes small, and the deformation performance deteriorates. Furthermore, the austenite crystal grains may become coarse and the low temperature toughness may deteriorate. Therefore, the heating temperature is desirably 1200 ° C. or lower. The heating temperature is more preferably 1100 ° C. or lower.

  Rolling is preferably performed under the condition that the total rolling reduction in a temperature range of 900 ° C. or lower is 50% or more. The rolling finishing temperature is preferably 850 to 700 ° C.

  By setting the total rolling reduction in the temperature range of 900 ° C. or less to 50% or more, it is possible to reliably impart residual strain to the austenite and to ensure good toughness. The total rolling reduction in the temperature range of 900 ° C. or lower is more preferably 75% or higher. Here, the “total rolling reduction in a temperature range of 900 ° C. or lower” is {(thickness when reaching 900 ° C.) − (Final thickness)} / (thickness when reaching 900 ° C.) × 100 (%) is meant.

  Furthermore, favorable intensity | strength and toughness are obtained more reliably by making rolling finishing temperature into 850-700 degreeC. That is, when the rolling finishing temperature is less than 700 ° C., the strength of the steel sheet may be insufficient, while when it exceeds 850 ° C., it may be difficult to ensure good toughness. The rolling finishing temperature is more preferably 730 ° C. or higher. The rolling finishing temperature is more preferably 800 ° C. or lower.

  In accelerated cooling after rolling, the cooling start temperature is preferably 850 to 700 ° C.

  The accelerated cooling after rolling is performed in order to obtain a predetermined tensile strength. If the cooling start temperature is less than 700 ° C., this effect may be reduced. On the other hand, if the cooling start temperature exceeds 850 ° C., good toughness may not be obtained. The upper limit of the cooling start temperature is preferably 800 ° C. The lower limit is preferably 750 ° C.

  In addition, in order to suppress generation | occurrence | production of a hydrogen crack, it is preferable that the cooling stop temperature shall be 200 degreeC or more. In addition, it is preferable to cool or slowly cool after stopping the cooling.

  In accelerated cooling after rolling, the cooling rate is preferably 10 ° C./s or more. If the cooling rate is less than 10 ° C./s, it may be difficult to ensure a predetermined tensile strength. In order to obtain a predetermined tensile strength more reliably, the cooling rate is preferably 20 ° C./s or more. In order to ensure good ductility of the steel sheet, the cooling rate is preferably 70 ° C./s or less.

  Each temperature mentioned above refers to the average temperature in the surface portion of the material to be rolled, and the “cooling rate” is a value obtained by dividing the temperature difference of the surface portion of the material at the start and stop of cooling by the cooling time. Point to. Here, the temperature when cooling is stopped means the maximum temperature reached after recuperation. However, when the cooling stop temperature is lower than 200 ° C., the temperature at the position in the thickness direction 1/4 (width direction 1/2 and length direction 1/2) of the material is used to start cooling. The cooling rate up to 200 ° C. is calculated. Moreover, accelerated cooling time means immersion time, when cooling in a water tank, for example.

  A line pipe can be produced by forming the steel plate produced in the present invention into a tubular shape, joining the butt portions, and applying a coating for expanding the tube and preventing corrosion as necessary.

  EXAMPLES Hereinafter, although an Example demonstrates this invention more concretely, this invention is not limited to these Examples.

  Using a steel piece having a chemical composition shown in Table 1 having a thickness of 140 mm, heating, rolling and accelerated cooling (water cooling) were performed under the production conditions shown in Table 2 to obtain a steel plate having a thickness of 19 mm. In addition, each temperature shown in Table 2 is the surface temperature of the material to be rolled on the entry side of each pass measured using a radiation thermometer. Further, the thickness of the steel plate on the exit side of each pass is as follows. First pass: 130 mm, Second pass: 110 mm, Third pass: 92 mm, Fourth pass: 76 mm, Fifth pass: 64 mm, Sixth pass: 54 mm The pass: 45 mm, the 8th pass: 38 mm, the 9th pass: 32 mm, the 10th pass: 27 mm, the 11th pass: 23 mm, the 12th pass: 21 mm, and the 13th pass: 19 mm.

  About each obtained steel plate, the tensile characteristic and the impact characteristic were investigated.

  Tensile properties are as follows: A round bar tensile test piece with a parallel part diameter of 8.5 mm and a gauge distance of 42.5 mm was taken in parallel to the rolling direction from the center of the plate thickness and subjected to a tensile test at room temperature. investigated. Specifically, 0.5% yield strength, tensile strength, uniform elongation, total elongation and drawing were determined, and the yield ratio (0.5% yield strength / tensile strength) was calculated from these results.

  After applying 0.5% tensile prestrain (nominal strain) to the tensile test piece, heat treatment was performed at 250 ° C. for 5 minutes in a salt bath, and the tensile properties after aging were similarly investigated. This condition is a condition that is stricter than the strain aging condition by normal pipe making and coating (that is, the degree of strain aging is large and the deformation performance is easily impaired).

  Impact characteristics were measured by taking a V-notch specimen described in JIS Z 2242 (2005) perpendicularly to the rolling direction from the center of the plate thickness, performing a Charpy impact test, and at a fracture surface transition temperature and at -80 ° C. Absorbed energy was determined.

  Each test result is shown in Table 3 together with the P value.

  As shown in Table 3, No. satisfying the conditions defined in the present invention. 2-5, 8-10, 12-21 are TS × U. El is 6000 or more and is excellent in the balance between tensile strength and uniform elongation. On the other hand, no. 1 and no. In No. 7, the chemical composition does not satisfy the conditions defined in the present invention. No. No. 11 has a high water cooling stop temperature of 440 ° C., which is outside the conditions defined in the present invention. No. 6, the chemical composition does not satisfy the conditions defined in the present invention, and the parameter P value is as small as 5.8. No. In No. 22, the chemical composition and the water cooling stop temperature are within the range defined by the present invention, but the P value is as small as 5.6. For this reason, these steel plates are TS × U. El is low.

  As described above, it is possible to produce a steel product for a line pipe having excellent strain aging resistance and a tensile strength of 760 MPa or more by the method of the present invention. This steel material is suitable as a material for a large-diameter, high-strength, high-toughness line pipe used for pipelines that transport natural gas and crude oil in large quantities.

Claims (3)

In mass%, C: more than 0.07% and 0.14% or less, Si: 0.2-0.9%, Mn: 1.0-3.0%, Cu: 0.05-1.0% , Ni: 0.05 to 1.5%, Mo: 0.04 to 0.20%, Nb: 0.005 to 0.08%, Ti: 0.005 to 0.04% and sol. Al: 0.005 to 0.100% is contained, the balance is made of Fe and impurities, and P, S, N and O as impurities are respectively P: 0.02% or less, S: 0.005% or less, Using a steel slab or steel ingot having a chemical composition of N: 0.010% or less and O: 0.005% or less, the P value obtained from the formula (1) is 5.9 or more and accelerated cooling is stopped. A method for producing a steel material for a line pipe having a tensile strength of 760 MPa or more, wherein heating, rolling and accelerated cooling are performed under conditions where the temperature is 400 ° C or lower.
P = 24 + 66C + 2Si- 2Mo-0.005T h -0.02T r -0.002T c (1)
However, (1) the elements in the formula symbols (C, Si and Mo) are in the steel the content of respective elements (mass%), _{T h,} the heating temperature before rolling (° C.), _{T r} is the rolling Finishing temperature (° C.) and T _c mean accelerated cooling stop temperature (° C.), respectively.   The billet or steel ingot further contains one or more selected from Cr: 1.0% or less, V: 0.5% or less, and B: 0.01% or less in mass%. The manufacturing method of the steel material for line pipes of Claim 1.   The steel slab or the steel ingot further contains, in mass%, at least one selected from Ca: 0.01% or less, REM: 0.02% or less, and Mg: 0.008% or less. The manufacturing method of the steel materials for line pipes of Claim 1 or Claim 2.

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