US20120018056A1

US20120018056A1 - Thick-walled high-strength hot rolled steel sheet having excellent hydrogen induced cracking resistance and manufacturing method thereof

Info

Publication number: US20120018056A1
Application number: US13/146,751
Authority: US
Inventors: Kinya Nakagawa; Chikara Kami
Original assignee: JFE Steel Corp
Current assignee: JFE Steel Corp
Priority date: 2009-01-30
Filing date: 2010-01-29
Publication date: 2012-01-26
Also published as: CN102301015B; CN103276291A; KR101686257B1; WO2010087512A1; KR20110110278A; EP2392681A1; KR20160057492A; RU2478123C1; CN102301015A; CA2809171C; US20170088916A1; CA2750291A1; EP2392681B1; US9809869B2; EP2392681A4; CA2750291C; CA2809171A1; KR20140041929A

Abstract

A thick-walled high-strength hot rolled steel sheet having excellent hydrogen induced cracking resistance which is preferably used as a raw material for a high-strength welded steel pipe of X65 grade or more and a method of manufacturing the thick-walled high-strength hot rolled steel sheet are provided. The composition of the thick-walled high-strength hot rolled steel sheet contains by mass % 0.02 to 0.08% C, 0.50 to 1.85% Mn, 0.03 to 0.10% Nb, 0.001 to 0.05% Ti, 0.0005% or less B in such a manner that (Ti+Nb/2)/C<4 is satisfied or also contains one or two kinds or more of 0.010% or less Ca, 0.02% or less REM, and Fe and unavoidable impurities as a balance. The steel sheet has the structure formed of a bainitic ferrite phase or a bainite phase. Surface layer hardness is 230HV or less in terms of Vickers hardness.

Description

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is the U.S. National Phase application of PCT International Application No. PCT/JP2010/051647, filed Jan. 29, 2010, and claims priority to Japanese Patent Application No. 2009-019339, filed Jan. 30, 2009, and Japanese Patent Application No. 2009-019342, filed Jan. 30, 2009, the disclosure of which PCT and priority applications are incorporated herein by reference in their entirely for all purposes.

FIELD OF THE INVENTION

The present invention relates to a thick-walled high-strength hot rolled steel sheet which is preferably used as a raw material for manufacturing a high strength welded steel pipe which is required to possess high toughness when used as a line pipe for transporting crude oil, a natural gas or the like and a manufacturing method thereof, and more particularly to the enhancement of low-temperature toughness and hydrogen induced cracking resistance. Here, in this specification, “thick-walled steel sheet” means a steel sheet having a sheet thickness of not less than 8.7 mm and not more than 35.4 mm. Further, “steel sheet” is a concept which includes a steel sheet and a steel strip.

BACKGROUND OF THE INVENTION

Recently, in view of sharp rise of crude oil price since oil crisis, demands for versatility of sources of energy or the like, the drilling for oil and a natural gas and the pipeline construction in a very cold land such as the North Sea, Canada and Alaska have been actively promoted. Further, with respect to a pipeline, there has been observed a trend where a high-pressure operation is performed using a large-diameter pipe to enhance transport efficiency of a natural gas or oil. To withstand a high-pressure operation in a pipeline, it is necessary to form a transport pipe (line pipe) using a thick steel pipe so that a UOE steel pipe which uses a plate as a raw material is used.
Recently, however, along with strong demands for the further reduction of construction cost of a pipeline, demands for the reduction of a material cost of steel pipes are strong. Accordingly, as a transport pipe, in place of a UOE steel pipe which uses a plate as a raw material, a high strength welded steel pipe which is formed using a coil-shaped hot rolled steel sheet (hot rolled steel strip) which possesses high productivity and can be produced at a lower cost as a raw material has been used.
These high strength welded steel pipes are required to possess high strength and, at the same time, excellent low-temperature toughness from a viewpoint of preventing bust-up of a line pipe. To manufacture such a steel pipe which possesses both of high strength and high toughness, attempts have been made to impart higher strength to a steel sheet which is a raw material of a steel pipe by transformation strengthening which makes use of accelerated cooling after hot rolling, precipitation strengthening which makes use of precipitates of alloy elements such as Nb, V, Ti or the like, and attempts have been made to impart higher toughness to the steel sheet through the formation of microstructure by making use of controlled rolling or the like.
Further, a transport pipe (line pipe) which is used for transporting crude oil or a natural gas which contains hydrogen sulfide is required to be excellent in so-called sour gas resistances such as hydrogen introduced cracking resistance (HIC resistance) or stress corrosion cracking resistance in addition to properties such as high strength and high toughness.
To satisfy such a demand, patent document 1, for example, proposes a method of manufacturing a high strength line-pipe-use steel sheet which possesses excellent hydrogen induced cracking resistance. A technique disclosed in patent document 1 is directed to a method of manufacturing a steel sheet for a high-strength electric resistance welded steel pipe of APIX 70 grade or more. That is, patent document 1 describes a method of manufacturing a steel sheet for a high-strength line pipe having excellent hydrogen induced cracking resistance, wherein a slab is heated at a temperature of 1000° C. to 1200° C. and is subjected to hot rolling thus forming a steel sheet, the steel sheet is cooled down such that a surface temperature of the steel sheet becomes a temperature of 500° C. or below by accelerated cooling after hot rolling is finished, the accelerated cooling is stopped once and the steel sheet is reheated such that the surface temperature of the steel sheet becomes a temperature of 500° C. or above and, thereafter, the steel sheet is cooled down to a temperature of 600° C. or below by accelerated cooling at a cooling rate of 3 to 50° C./s. The technique described in patent document 1 adopts intermittent accelerated cooling so that the temperature distribution in the steel sheet becomes uniform in the sheet thickness direction and, at the same time, the hardened structure formed on a surface side is subjected to tempering so that the hydrogen induced cracking resistance of a high strength steel sheet can be enhanced while suppressing the increase of hardness of the steel sheet in the vicinity of a surface of the steel sheet.
Further, patent document 2 proposes a method of manufacturing a high strength steel plate which possesses excellent hydrogen induced cracking resistance. A technique disclosed in patent document 2 is directed to a method of manufacturing a steel sheet for a high-strength steel pipe of APIX 60 grade or more. That is, patent document 2 describes a method of manufacturing a high strength steel plate having excellent hydrogen induced cracking resistance, wherein a slab is heated at a temperature of 1000° C. to 1200° C., the slab is subjected to rolling at a reduction rate of 60% or more in an austenite temperature range of 950° C. or below, a steel plate formed by rolling is cooled from (Ar₃−50° C.) or above until a surface temperature of the steel plate becomes 500° C. or below at an average cooling rate of 5 to 20° C./s at a center portion of the steel plate, and the steel plate is cooled to 600° C. or below at an average cooling rate of 5 to 50° C./s at the center portion of the steel plate. The technique described in patent document 2 adopts two-stage cooling which changes a cooling rate in the midst of cooling so that the steel plate can secure desired strength while suppressing hardness of the steel plate in the vicinity of a surface of the steel plate.

PATENT DOCUMENT

[Patent document 1] JP-A-11-80833
[Patent document 2] JP-A-2000-160245

SUMMARY OF THE INVENTION

However, recently, demands for a transport pipe (line pipe) are becoming stricter so that the further improvement of sour resistance of the transport pipe is requested, and the further lowering of surface hardness is requested. The techniques described in patent documents 1 and 2 cannot lower the hardness of a surface layer of the steel sheet to an extent that the recent strict demand for hydrogen induced cracking resistance is satisfied thus giving rise to a drawback that a steel sheet for a high strength welded steel pipe of X65 grades or more which possesses the excellent hydrogen induced cracking resistance cannot be manufactured in a stable manner.
The present invention has been made to overcome the above-mentioned drawbacks, and it aims to provide a thick-walled high-strength hot rolled steel sheet with which a high-strength welded steel pipe of X65 grade or more can be manufactured and possesses excellent hydrogen induced cracking resistance, and a method of manufacturing the thick-walled high-strength hot rolled steel sheet.
Inventors of the present invention have made studies extensively on various factors which influence surface layer hardness. As a result, the inventors have found that it is possible to stably manufacture a thick-walled high-strength hot rolled steel sheet having tensile strength of 520 MPa or more by which a high strength welded steel pipe of X65 grade or more having low surface layer hardness of 230HV or less can be manufactured in the following manner. That is, in manufacturing the hot rolled steel sheet by applying hot rolling consisting of rough rolling and finish rolling to a raw steel material having composition which contains C, Nb, Ti such that C, Nb, Ti satisfy a specific relational formula or in which alloy element quantities are adjusted such that at least one of a carbon equivalent Ceq or Pcm takes a predetermined value or less, the steel sheet is cooled by applying intermittent cooling to the steel sheet after the finish rolling is finished.
The inventors of the present invention have made further studies based on the above-mentioned finding and have made the present invention.
Embodiments of the present invention are described as follows.
A thick-walled high-strength hot rolled steel sheet is provided having a composition which contains by mass % 0.02 to 0.08% C, 1.0% or less Si, 0.50 to 1.85% Mn, 0.03% or less P, 0.005% or less S, 0.1% or less Al, 0.02 to 0.10% Nb, 0.001 to 0.05% Ti, 0.0005% or less B, and Fe and unavoidable impurities as a balance, wherein the steel sheet contains Nb, Ti and C in such a manner that a following formula (1) is satisfied, the steel sheet has the structure formed of a bainitic ferrite phase or a bainite phase, and surface layer hardness is 230HV or less in terms of Vickers hardness.
(Ti+Nb/2)/C<4 (1)
Here, Ti, Nb, C: contents of respective elements (mass %)
In the thick-walled high-strength hot rolled steel sheet, the composition optionally further contains by mass % one or two kinds or more selected from a group consisting of 0.5% or less V, 1.0% or less Mo, 1.0% or less Cr, 4.0% or less Ni, and 2.0% or less Cu in addition to the above-mentioned composition.
The composition optionally further contains by mass % one or two kinds or more selected from a group consisting of 0.010% or less Ca, 0.02% or less REM, and 0.003% or less Mg in addition to the above-mentioned composition.
The composition optionally further satisfies at least one of a condition that Ceq defined by a following formula (2) is 0.32% or less and a condition that Pcm defined by a following formula (3) is 0.130% or less.
Ceq=C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15 (2)
Pcm=C+Si/30+(Mn+Cu+Cr)/20+Ni/60+Mo/15+V/10+5B (3)
Here, C, Si, Mn, Cr, Mo, V, Cu, Ni, B: contents of respective elements (mass %)
A method of manufacturing a thick-walled high-strength hot rolled steel sheet having surface layer hardness of 230HV or less in terms of Vickers hardness and having excellent hydrogen induced cracking resistance is also provided, wherein in manufacturing a hot rolled steel sheet by applying hot rolling consisting of rough rolling and finish rolling to a raw steel material having the composition according to the above-mentioned steel sheet, after the finish rolling is finished, a first cooling step in which the hot rolled steel sheet is cooled by accelerated cooling at an average surface cooling rate of 30° C./s or more until a surface temperature becomes 500° C. or below, a second cooling step in which the hot rolled steel sheet is cooled by air cooling for 10s or less after the first cooling step is finished, and a third cooling step in which the hot rolled steel sheet is cooled by accelerated cooling to a temperature which falls within a temperature range from 350° C. or above to a temperature below 600° C. at the center of a sheet-thickness at an average cooling rate of 10° C./s or more at the center of the sheet-thickness are applied to the hot rolled steel sheet, and the hot rolled steel sheet is coiled in a coil shape after the third cooling step is finished.
The accelerated cooling in the third cooling step is optionally cooling performed at a heat flow rate of 1.5 Gcal/m²hr or more in entire surface nuclear boiling.
In the method of manufacturing a thick-walled high-strength hot rolled steel sheet, the composition optionally further contains by mass % one or two kinds or more selected from a group consisting of 0.5% or less V, 1.0% or less Mo, 1.0% or less Cr, 4.0% or less Ni, and 2.0% or less Cu in addition to the above-mentioned composition.
The composition optionally further contains by mass % one or two kinds or more selected from a group consisting of 0.010% or less Ca, 0.02% or less REM, and 0.003% or less Mg in addition to the above-mentioned composition.
In the method of manufacturing a thick-walled high-strength hot rolled steel sheet, the composition optionally further satisfies at least one of a condition that Ceq defined by a following formula (2) is 0.32% or less and a condition that Pcm defined by a following formula (3) is 0.13% or less.
Ceq=C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15 (2)
Pcm=C+Si/30+(Mn+Cu+Cr)/20+Ni/60+Mo/15+V/10+5B (3)
Here, C, Si, Mn, Cr, Mo, V, Cu, Ni, B: contents of respective elements (mass %)
A method of manufacturing a thick-walled high-strength hot rolled steel sheet having tensile strength of 520 MPa or more and a surface layer hardness of 230HV or less in terms of Vickers hardness and having excellent hydrogen induced cracking resistance is provided, wherein in manufacturing a hot rolled steel sheet by applying hot rolling consisting of rough rolling and finish rolling to a raw steel material having the composition according to the above-mentioned steel sheet, after the finish rolling is finished, a first cooling step in which the hot rolled steel sheet is cooled by accelerated cooling at an average cooling rate of 20° C./s or more and less than a martensite formation critical cooling rate on a surface of the hot rolled steel sheet until a surface temperature becomes a temperature not more than an A_r3transformation temperature and not less than an Ms temperature, a second cooling step in which the hot rolled steel sheet is rapidly cooled to a temperature within a temperature range from 350° C. or above to a temperature below 600° C. at the center of a sheet-thickness after the first cooling step is finished, and a third cooling step in which, after the second cooling step is finished, the hot rolled steel sheet is coiled in a coil shape at a coiling temperature falling within a temperature range from 350° C. or above to a temperature below 600° C. in terms of a temperature at the center of sheet-thickness and, thereafter, a temperature of the hot rolled steel sheet at least at a position of ¼ sheet-thickness to ¾ sheet-thickness in a coil thickness direction is held or kept within a temperature range from 350° C. or above to a temperature below 600° C. for 30 min or more are sequentially applied to the hot rolled steel sheet.
The rapid cooling in the second cooling step is optionally cooling at a heat flow rate of 1.0 Gcal/m²hr or more in entire surface nuclear boiling.
The composition optionally further contains by mass % one or two kinds or more selected from a group consisting of 0.5% or less V, 1.0% or less Mo, 1.0% or less Cr, 4.0% or less Ni, and 2.0% or less Cu in addition to the above-mentioned composition.
The composition optionally further contains by mass % one or two kinds selected from a group consisting of 0.010% or less Ca, 0.02% or less REM, 0.003% or less Mg in addition to the above-mentioned composition.
The composition optionally further satisfies at least one of a condition that Ceq defined by a following formula (2) is 0.32% or less and a condition that Pcm defined by a following formula (3) is 0.13% or less.
Ceq=C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15 (2)
Pcm=C+Si/30+(Mn+Cu+Cr)/20+Ni/60+Mo/15+V/10+5B (3)
Here, C, Si, Mn, Cr, Mo, V, Cu, Ni, B: contents of respective elements (mass %)
According to an embodiment of the present invention, the high-strength hot rolled steel sheet which possesses high strength of tensile strength: 520 MPa or more and low surface hardness of 230HV or less, has a large sheet thickness of 8.7 mm or more, possesses excellent hydrogen induced cracking resistance, and can be preferably used as a raw material for a high strength welded steel pipe can be manufactured in a stable manner whereby the present invention can acquire an outstanding industrial advantageous effect. Further, by using the hot rolled steel sheet manufactured by the present invention as a raw material, the present invention can also acquire an advantageous effect that the high strength welded steel pipe possessing excellent hydrogen induced cracking resistance of X65 grade or more can be manufactured at a low cost and also in a stable manner.

DETAILED DESCRIPTION OF THE INVENTION

Firstly, the reason that the composition of the raw steel materials used in embodiments of the present invention may be limited is explained. Unless otherwise specified, mass % is simply described as %.

C: 0.02 to 0.08%

C is an element which performs the action of increasing strength of steel. The hot rolled steel sheet preferably contains 0.02% or more of C for securing desired high strength. On the other hand, when the content of C exceeds 0.08%, a structural fraction of a secondary phase such as pearlite is increased so that base material toughness and toughness of a welded heat affected zone are deteriorated. Accordingly, the content of C is limited to a value which falls within a range from 0.02 to 0.08%. The content of C is preferably limited to a value which falls within a range from 0.03 to 0.05%.

Si: 1.0% or Less

Si is a deoxidizer and also performs the action of increasing strength of steel through solution strengthening and the enhancement of hardenability. Such an advantageous effect can be acquired when the content of Si is 0.01% or more. On the other hand, when the content of Si exceeds 1.0%, oxide which contains Si is formed at the time of electric resistance welding so that quality of a welded portion is deteriorated and, at the same time, toughness of a welded heat affected zone is deteriorated. Accordingly, the content of Si is limited to 1.0% or less. The content of Si is preferably limited to 0.1 to 0.4%.

Mn: 0.50 to 1.85%

Mn performs the action of enhancing hardenability so that Mn increases strength of the steel sheet through the enhancement of hardenability. Further, Mn forms MnS thus fixing S and hence, the grain boundary segregation of S is prevented whereby cracking of slab (raw steel material) can be suppressed. To acquire such an advantageous effect, it is advantageous to set the content of Mn to 0.50% or more. On the other hand, when the content of Mn exceeds 1.85%, weldability, and hydrogen induced cracking resistance are deteriorated. Further, when the content of Mn is large, solidification segregation at the time of casting slab is promoted so that Mn concentrated parts remain in a steel sheet so that the occurrence of separation is increased. To dissipate the Mn concentrated parts, it is advantageous to heat the hot rolled steel sheet at a temperature exceeding 1300° C. and it is unrealistic to carry out such heat treatment in an industrial scale. Accordingly, the content of Mn is limited to a value which falls within a range from 0.50 to 1.85%. The content of Mn is preferably limited to a value which falls within a range from 0.8 to 1.2%.

P: 0.03% or Less

Although P is contained in steel as an unavoidable impurity, P performs the action of increasing strength of steel. However, when P is contained excessively exceeding 0.03%, weldability is deteriorated. Accordingly, the content of P is limited to 0.03% or less. The content of P is preferably limited to 0.01% or less.

S: 0.005% or Less

S is also contained in steel as an unavoidable impurity in the same manner as P. However, when S is contained exceeding 0.005%, cracks occur in slab, and coarse MnS is formed in a hot rolled steel sheet thus deteriorating ductility. Accordingly, the content of S is limited to 0.005% or less. The content of S is preferably limited to 0.001% or less.

Al: 0.1% or Less

Al is an element which acts as a deoxidizes and, to acquire such an advantageous effect, it is desirable to set the content of Al to 0.005% or more, and it is more desirable to set the content of Al to 0.01% or more. On the other hand, when the content of Al exceeds 0.1%, cleanability of a welded part at the time of electric resistance welding is remarkably deteriorated. Accordingly, the content of Al is limited to 0.1% or less. The content of Al is preferably limited to a value which falls within a range from 0.005 to 0.05%.

Nb: 0.02 to 0.10%

Nb is an element which performs the action of suppressing the coarsening and the recrystallization of austenite. Nb enables rolling in an austenite un-recrystallization temperature range in hot finish rolling and is finely precipitated as carbonitride so that Nb performs the action of increasing strength of hot rolled steel sheet with the small content without deteriorating weldability. To acquire such advantageous effects, it is advantageous to set the content of Nb to 0.03% or more. On the other hand, when the content of Nb exceeds 0.10%, a rolling load during hot finish rolling is increased and hence, there may be a case where hot rolling becomes difficult. Accordingly, the content of Nb is limited to a value which falls within a range from 0.02 to 0.10%. The content of Nb is preferably limited to a value which falls within a range from 0.03% to 0.07%. The content of Nb is more preferably limited to a value which falls within a range from 0.04% to 0.06%.

Ti: 0.001 to 0.05%

Ti performs the action of preventing cracks in slab (raw steel material) by forming nitride thus fixing N, and is also finely precipitated as carbide so that strength of a steel sheet is increased. Although such an advantageous effect becomes outstanding when the content of Ti is 0.001% or more, when the content of Ti exceeds 0.05%, a yield point is remarkably elevated due to precipitation strengthening. Accordingly, the content of Ti is limited to a value which falls within a range from 0.001 to 0.05%. The content of Ti is preferably limited to a value which falls within a range from 0.005% to 0.03%.
In the present invention, the hot rolled steel sheet preferably contains Nb, Ti, C which fall within the above-mentioned ranges, and the contents of Nb, Ti, C are adjusted such that the following formula (1) is satisfied.
(Ti+Nb/2)/C<4 (1)
Nb, Ti are elements which have strong carbide forming tendency, wherein most of C is turned into carbide when the content of C is low, and the drastic decrease of solid-solution C content in ferrite grains is considered. The drastic decrease of solid-solution C content in ferrite grains adversely influences circumferential weldability (girth welding property) of a steel pipe at the time of constructing pipelines. When girth welding is applied to a steel pipe which is manufactured using a steel sheet in which the solid-solution C content in ferrite grains is extremely lowered as a line pipe, the grain growth in a heat affected zone (HAZ) of a girth welded part becomes conspicuous thus giving rise to a possibility that toughness of the heat affected zone of the girth welded part is deteriorated. Accordingly, the contents of Nb, Ti, C are preferably adjusted so as to satisfy the formula (1). Due to such adjustment, the solid-solution C content in ferrite grains can be set to 10 ppm or more and hence, the deteriorating of toughness of the heat affected zone of the girth weld portion can be prevented.

B: 0.0005% or Less

B is an element which has a strong tendency of generating segregation in a grain boundary and contributes to the increase of strength of steel through the enhancement of hardenability. This advantageous effect can be acquired when the content of B is 0.0001% or more. However, toughness of steel is deteriorated when the content of B exceeds 0.0005%. Accordingly, the content of B is limited to 0.0005% or less.
Although the above-mentioned contents are basic contents of the hot rolled steel sheet, in addition to the basic composition, the hot rolled steel sheet may selectively contain one or two kinds or more selected from a group consisting of 0.5% or less V, 1.0% or less Mo, 1.0% or less Cr, 4.0% or less Ni and 2.0% or less Cu and/or one or two kinds selected from a group consisting of 0.010% or less Ca, 0.02% or less REM and 0.003% or less Mg if necessary.
One or two kinds or more selected from a group consisting of 0.5% or less V, 1.0% or less Mo, 1.0% or less Cr, 4.0% or less Ni and 2.0% or less Cu
All of V, Mo, Cr, Ni and Cu are elements which enhance hardenability and increase strength of the steel sheet, and the hot rolled steel sheet may contain one or two kinds or more selected from these elements when necessary.
V is an element which performs the action of increasing strength of a steel sheet through the enhancement of hardenability and the formation of carbonitride. Such an advantageous effect becomes outstanding when the content of V is 0.01% or more. On the other hand, when the content of V exceeds 0.5%, the weldability is deteriorated. Accordingly, the content of V is preferably limited to 0.5% or less. The content of V is more preferably limited to 0.08% or less.
Mo is an element which performs the action of increasing strength of a steel sheet through the enhancement of hardenability and the formation of carbonitride. Such an advantageous effect becomes outstanding when the content of Mo is 0.01% or more. On the other hand, when the content of Mo exceeds 1.0%, the weldability is deteriorated. Accordingly, the content of Mo is preferably limited to 1.0% or less. The content of Mo is more preferably limited to a value which falls within a range from 0.05 to 0.35%.
Cr is an element which performs the action of increasing strength of a steel sheet through the enhancement of hardenability. Such an advantageous effect becomes outstanding when the content of Cr is 0.01% or more. On the other hand, when the content of Cr exceeds 1.0%, there arises a tendency that a welding defect frequently occurs at the time of electric resistance welding. Accordingly, the content of Cr is preferably limited to 1.0% or less. The content of Cr is more preferably limited to less than 0.30%.
Ni is an element which performs the action of increasing strength of steel through the enhancement of hardenability and also performs the action of enhancing toughness of a steel sheet. To acquire such an advantageous effect, the content of Ni is preferably set to 0.01% or more. However, even when the content of Ni exceeds 4.0%, the advantageous effect is saturated so that an advantageous effect corresponding to the content is not expected whereby the content of Ni exceeding 4.0% is economically disadvantageous. Accordingly, the content of Ni is preferably limited to 4.0% or less. The content of Ni is more preferably limited to a value which falls within a range from 0.10 to 1.0%.
Cu is an element which performs the action of increasing strength of a steel sheet through the enhancement of hardenability and solution strengthening or precipitation strengthening. To acquire such an advantageous effect, the content of Cu is desirably set to 0.01% or more. However, when the content of Cu exceeds 2.0%, hot-rolling workability is deteriorated. Accordingly, the content of Cu is preferably limited to 2.0% or less. The content of Cu is more preferably limited to a value which falls within a range from 0.10 to 1.0%.
One or two kinds selected from a group consisting of 0.010% or less Ca, 0.02% or less REM, 0.003% or less Mg
All of Ca, REM and Mg are elements which contribute to a shape control of sulfide for forming spread coarse sulfide into spherical sulfide, and the composition can selectively contain these elements when necessary. To acquire such an advantageous effect, it is desirable that the composition contains 0.001% or more of Ca, 0.001% or more of REM. However, when the content of Ca exceeds 0.010% or the content of REM exceeds 0.02%, cleanliness of the steel sheet is deteriorated. Accordingly, it is desirable to limit the content of Ca to 0.010% or less and the content of REM to 0.02% or less.
It is preferable that the composition contains Ca within the above-mentioned range, and the content of Ca is adjusted such that ACR which is defined by the following formula satisfies 1.0 to 4.0 in terms of contents of O and S.
ACR={Ca−O×(0.18+130Ca)}/1.25S
(here, Ca, O, S: contents of respective elements (mass %))
Accordingly, deteriorating of corrosion resistance and corrosion cracking resistance is prevented even under a sour environment.
Mg is, in the same manner as Ca or the like, an element which forms sulfide or oxide, suppresses the formation of coarse sulfide MnS, and contributes to a shape control of sulfide. The composition may contain Mg when necessary. Such advantageous effects can be acquired when the content of Mg is 0.0005% or more. However, when the content of Mg exceeds 0.003%, clusters of Mg oxide or Mg sulfide are formed thus deteriorating toughness of the steel sheet. Accordingly, when the composition contains Mg, it is preferable to limit the content of Mg to 0.003% or less.
It is preferable that the composition of the hot rolled steel sheet contains the above-mentioned components within the above-mentioned ranges respectively, and the composition is adjusted such that Ceq defined by a following formula (2) satisfies 0.32% or less, or Pcm defined by a following formula (3) satisfies 0.13% or less.
Ceq=C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15 (2)
(here, C, Si, Mn, Cr, Mo, V, Cu, Ni: contents of respective elements (mass %))
Pcm=C+Si/30+(Mn+Cu+Cr)/20+Ni/60+Mo/15+V/10+5B (3)
(here, C, Si, Mn, Cr, Mo, V, Cu, Ni, B: contents of respective elements (mass %))
When Ceq exceeds 0.32% or Pcm exceeds 0.13%, it becomes difficult to adjust the composition such that hardness of a surface layer becomes 230HV or less, and also hardenability becomes high so that circumferential welded part toughness is deteriorated.
The balance other than the above-mentioned components is constituted of Fe and unavoidable impurities.
As unavoidable impurities, the steel sheet is allowed to contain 0.005% or less O, 0.008% or less N, and 0.005% or less Sn.

O: 0.005% or Less

O forms various oxides in steel and deteriorates hot-rolling workability, corrosion resistance, toughness and the like. Accordingly, it is desirable to reduce the content of O as much as possible. However, since the extreme reduction of O brings about the sharp rise of a refining cost, the steel sheet is allowed to contain up to 0.005% O.

N: 0.008% or Less

Although N is an element which is unavoidably contained in steel, the excessive content of N frequently causes cracks at the time of casting a slab. Accordingly, it is desirable to reduce the content of N as much as possible. However, the steel sheet is allowed to contain up to 0.008% N.

Sn: 0.005% or Less

Sn is an element which is mixed into the steel sheet from the scrap used as a steel-making raw material and is unavoidably contained in steel. Sn is an element which is liable to be segregated in a grain boundary or the like and hence, when the content of Sn becomes large, grain boundary strength is deteriorated thus deteriorating toughness. However, the steel sheet is allowed to contain up to 0.005% Sn.
Here, as a method of manufacturing a raw steel material, it is preferable to manufacture the raw steel material in such a manner that molten steel having the above-mentioned composition is produced by a usual melting method such as a converter, and molten metal is cast into the raw steel material such as slab by a usual casting method such as a continuous casting method. However, the present invention is not limited to such a method.
The raw steel material having the above-mentioned composition is heated and is subjected to hot rolling thus forming a hot rolled steel sheet (steel strip).
As a method of manufacturing a raw steel material, it is preferable to manufacture the raw steel material in such a manner that molten steel having the above-mentioned composition is produced by a usual melting method such as a converter, and molten metal is cast into the raw steel material such as slab by a usual casting method such as a continuous casting method. However, the present invention is not limited to such a method.
The hot rolling is constituted of rough rolling which turns the raw steel material (slab) into a sheet bar by heating, and finish rolling which turns the sheet bar into a hot rolled steel sheet.
Although heating temperature of a raw steel material (slab) is not necessarily limited provided that the raw steel material (slab) can be rolled into a hot rolled steel sheet, the heating temperature is preferably set to a temperature which falls within a range from 1000 to 1300° C. When the heating temperature is below 1000° C., the deformation resistance is high so that a rolling load is increased whereby a load applied to a rolling mill becomes excessively large. On the other hand, when the heating temperature becomes high exceeding 1300° C., crystal grains become coarse so that low-temperature toughness is deteriorated, and a scale generation amount is increased so that a yield is lowered. Accordingly, the heating temperature in hot rolling is preferably set to a temperature which falls within a range from 1000 to 1300° C. The heating temperature is more preferably set to a temperature which falls within a range from 1050 to 1250° C.
A sheet bar is formed by applying rough rolling to the heated raw steel material (slab). Conditions for rough rolling are not necessarily limited provided that the sheet bar of desired size and shape can be obtained.
Finish rolling is further applied to the obtained sheet bar thus forming a hot rolled steel sheet.
In finish rolling, from a viewpoint of enhancing toughness, finish rolling completion temperature is preferably set to (A_C3−50° C.) or less and 800° C. or less, and a total rolling reduction rate (%) in a temperature range of 1000° C. or below is preferably set to 60% or more. This is because when the finish rolling completion temperature falls outside the above-mentioned finish rolling completion temperature range or when the total rolling reduction rate in the temperature range of 1000° C. or below is less than 60%, fine structure cannot be obtained and hence, toughness is deteriorated.
The hot rolled steel sheet has the structure formed of a bainitic ferrite phase or bainite phase, and surface layer hardness of the steel sheet is 230HV or less in terms of Vickers hardness. To acquire such a steel sheet, the present invention provides, as a basic step, the method of manufacturing a thick-walled high-strength hot rolled steel sheet having a surface layer hardness of 230HV or less in Vickers hardness, wherein the cooling step which is performed after the finish rolling is constituted of the first cooling step in which the steel sheet is cooled by accelerated cooling immediately after completion of the finish rolling at the average surface cooling rate equal to or more than predetermined cooling rate such that the precipitation of polygonal ferrite on the surface of the steel sheet is prevented until the surface temperature becomes a temperature equal to or below the A_r3transformation temperature, and the second cooling step in which, after the first cooling step is finished, the steel sheet is cooled by accelerated cooling at the average cooling rate at the center of the sheet thickness to the temperature within the temperature range from 350° C. or above to a temperature below 600° C. at the center of the sheet thickness such that the precipitation of polygonal ferrite or pearlite at a sheet-thickness center portion is prevented, and the hot rolled steel sheet is coiled in a coil shape after the second cooling step is finished. Further, to further lower hardness of the surface of the steel sheet, a step of air cooling is performed between the first cooling step and the second cooling step or a step of holding or keeping the steel strip within a temperature range from 350° C. or above to a temperature below 600° C. for 30 minutes or more is performed after coiling.
As specific examples of a manufacturing method provided by the present invention, a first embodiment and a second embodiment are described hereinafter. The respective embodiments are explained in detail hereinafter.

First Embodiment

In the first embodiment, after being subjected to finish rolling, the hot rolled steel sheet is subjected to the first cooling step and the second cooling step subsequently, is subjected to the third cooling step thereafter, and is coiled in a coil shape after completion of the third cooling step.
In the first cooling step, immediately after the completion of the finish rolling, the hot rolled steel sheet is subjected to accelerated cooling at an average surface cooling rate of 30° C./s or more until the surface temperature becomes 500° C. or below. Here, “immediately after the finish rolling” means that cooling is started within 10s after the completion of the finish rolling.
A surface temperature control is performed in the accelerated cooling in the first cooling step. When the average surface cooling rate is less than 30° C./s, polygonal ferrite precipitates so that the hot rolled steel sheet cannot achieve the desired enhancement of strength and the desired enhancement of toughness. The preferred average surface cooling rate is 100 to 300° C./s. Also in the first cooling step, a cooling stop temperature in the acceleration cooing is set to a temperature equal to or below 500° C. in terms of the surface temperature. When the cooling stop temperature exceeds 500° C., there is a possibility that transformation on a surface layer is not completed so that the surface layer is transformed into a low-temperature transformation product material in the succeeding cooling step whereby it is no more possible to expect lowering of hardness of the surface layer.
In the second cooling step, air cooling is performed for 10s or less after completion of the first cooling step.
In this air cooling, the surface layer recovers heat due to heat which a center portion of the hot rolled steel sheet possesses and hence, the surface layer is tempered whereby lowering of hardness of the surface layer is accelerated. Further, air cooling also brings about an advantageous effect that the succeeding cooling of the hot rolled steel sheet at the center in the sheet thickness direction is enhanced. Even when the air cooling time is prolonged exceeding 10s, the above-mentioned advantageous effect is saturated, and productivity is lowered. Accordingly, air cooling time is limited to a value within 10s. From a viewpoint of enhancing productivity, the air cooling time is preferably set to 7s or less. Further, to acquire a tempering effect of the surface layer by recuperation, air cooling time is preferably set to is or more.
In the third cooling step, after completion of the second cooling step, the hot rolled steel sheet is subjected to accelerated cooling at an average cooling rate of 10° C./s or more at the center of the sheet thickness until the temperature at the center of the sheet thickness becomes a temperature in a temperature range from 350° C. or above to a temperature below 600° C. A sheet thickness center temperature control is performed in the accelerated cooling in the third cooling step.
When the average cooling rate at the center of the sheet thickness is less than 10° C./s, polygonal ferrite or pearlite is liable to precipitate so that the hot rolled steel sheet cannot acquire the desired enhancement of strength and the desired enhancement of toughness. Although an upper limit of the average cooling rate at the center of the sheet thickness is decided depending on performance of a cooling device in service, it is desirable to set the upper limit of the average cooling rate to 100° C./s or less which does not bring about deterioration of a shape of the steel sheet such as a warp.
From a viewpoint of securing toughness, the preferred average cooling rate at the center in the sheet thickness is 25° C./s or more. Such cooling can be achieved by cooling (cooling with water) the hot rolled steel sheet by entire surface nuclear boiling at a heat flow rate of 1.5 Gcal/m²hr or more.
The above-mentioned accelerated cooling is performed until the temperature at the center of sheet thickness becomes a temperature (cooling stop temperature) within a temperature range from 350° C. or above to a temperature below 600° C. When the cooling stop temperature falls outside this range, after winding the hot rolled steel sheet in a coil shape after accelerated cooling, the hot rolled steel sheet cannot be held within a predetermined temperature range for a predetermined time or more and hence, the hot rolled steel sheet cannot secure desired high strength and desired high toughness.
After being subjected to the third cooling step, the hot rolled steel sheet is coiled in a coil shape at a coiling temperature range from 350° C. or above to a temperature below 600° C.
By stopping the accelerated cooling at the above-mentioned cooling stop temperature and by coiling the hot rolled steel sheet in a coil shape at the above-mentioned coiling temperature, the hot rolled steel sheet can be held or kept within the temperature range from 350° C. or above to a temperature below 600° C. for 30 min or more and hence, the enhancement of precipitation is accelerated in the inside of the sheet whereby the hot rolled steel sheet can secure desired high strength and desired high toughness, while hardness of the hot rolled steel sheet at the surface of the hot rolled steel sheet can be lowered due to self annealing.

Second Embodiment

In the second embodiment, after being subjected to finish rolling, the hot rolled steel sheet is subjected to the first cooling step, the second cooling step and the third cooling step sequentially.
In the first cooling step, immediately after the completion of the finish rolling, the hot rolled steel sheet is subjected to accelerated cooling until the surface temperature of the hot rolled steel sheet becomes a temperature not more than A_r3transformation temperature and a martensite transformation temperature or more at an average cooling rate of not less than 20° C./s and less than a critical cooling rate of martensite formation. Here, “immediately after the completion of the finish rolling” means that cooling is started within 10s after completion of the finish rolling.
A surface temperature control is performed in the accelerated cooling in the first cooling step. When the average cooling rate of the surface of the hot rolled steel sheet is less than 20 C.°/s, polygonal ferrite precipitates so that the hot rolled steel sheet cannot achieve the desired enhancement of strength and the desired enhancement of toughness. It is preferable to set an upper limit of the average cooling rate of the surface of the hot rolled steel sheet to a rate less than a martensite formation critical cooling rate (approximately 100° C./s to 500° C./s with respect to the composition range described herein) in view of a purpose of preventing the formation of martensite to lower hardness of the surface layer. The preferred surface average cooling rate is 50 to 100° C./s. In the first cooling step, the cooling stop temperature in the accelerated cooling is set to an A_r3transformation temperature or below and above a martensite transformation temperature in terms of a surface temperature. When the cooling stop temperature exceeds the A_r3transformation temperature, there exists a possibility that the transformation in a surface layer region is not completed, and the surface layer is transformed into a low-temperature transformed product in the succeeding cooling step whereby it is no more possible to expect the lowering of hardness of the surface layer.
In the second cooling step, after completion of the first cooling step, the hot rolled steel sheet is rapidly cooled until the hot rolled steel sheet at the center of sheet thickness becomes a temperature within a temperature range from 350° C. or above to a temperature below 600° C. It is preferable to set the cooling rate in the rapid cooling to 10° C./s or more in terms of the average cooling rate at the sheet thickness center position. When the average cooling rate at the sheet thickness center position is less than 10° C./s, pearlite is liable to precipitate and hence, the hot rolled steel sheet cannot achieve the desired enhancement of strength and the desired enhancement of toughness. Although an upper limit of the average cooling rate at the center of sheet thickness is decided depending on performance of a cooling device in service, it is desirable to set the upper limit of the average cooling rate to 300° C./s or less which does not bring about deterioration of a shape of the steel sheet such as a warp. From a viewpoint of enhancing toughness, the preferred average cooling rate at the sheet thickness center position is 25° C./s or more. Such cooling can be achieved by cooling (cooling with water) the hot rolled steel sheet by entire surface nuclear boiling at a heat flow rate of 1.0 Gcal/m²hr or more. The temperature and the cooling rate at the sheet thickness center position are obtained by calculation based on the sheet thickness, the surface temperature and the heat flow rate.
The above-mentioned rapid cooling is performed until the temperature at the center of the sheet thickness becomes a temperature (cooling stop temperature) of 350° C. or above and below 600° C. When the cooling stop temperature is below 350° C., the succeeding normal coiling of the hot rolled steel sheet becomes impossible. On the other hand, when the coiling temperature is 600° C. or more, a grain size becomes coarse so that the hot rolled steel sheet cannot secure high strength and high toughness.
After being subjected to the second cooling step, the hot rolled steel sheet is coiled in a coil shape after the coiling temperature is adjusted to a temperature of 350° C. or above and below 600° C. in terms of a sheet thickness center temperature, and is subjected to the third cooling step where the hot rolled steel sheet at a position of ¼ sheet-thickness to ¾ sheet-thickness in the coil thickness direction is held or kept within a temperature range from 350° C. or above to a temperature below 600° C. for 30 min or more.
When the coiling temperature is below 350° C., the sheet temperature becomes excessively low and hence, it becomes difficult to coil the hot rolled steel sheet into a proper coiling shape. On the other hand, when the coiling temperature becomes high exceeding 600° C., crystal grains become coarse and hence, the hot rolled steel sheet cannot secure desired high strength and the desired high toughness. Accordingly, the coiling temperature is set to the temperature which falls within the range from 350° C. or more to a temperature below 600° C. in terms of the sheet thickness center temperature. The coiling temperature is preferably set to 450 to 550° C.
In the third cooling step, the hot rolled steel sheet coiled in a coil shape is subjected to cooling where the hot rolled steel sheet at least at the position of ¼ sheet thickness to ¾ sheet thickness in the thickness direction of the coil is held or kept within the temperature range from 350° C. or above to a temperature below 600° C. for 30 min or more. By stopping the rapid cooling at the above-mentioned cooling stop temperature and by coiling the hot rolled steel sheet in a coil shape at the above-mentioned coiling temperature, it is possible to perform cooling where the hot rolled steel sheet at the position of ¼ sheet thickness to ¾ sheet thickness in the coil thickness direction is held or kept within the temperature range from 350° C. or above to a temperature below 600° C. for 30 min or more by natural air cooling. However, to hold or keep the hot rolled steel sheet in the temperature region in a more reliable manner, it is preferable to heat the coil or to store the coil in a coil box or the like after the hot rolled steel sheet is coiled in a coil shape.
By making the coil subject to the cooling where the hot rolled steel sheet is held or kept within the temperature range from 350° C. or above to a temperature below 600° C. for 30 min or more, the precipitation is enhanced in the inside of the steel sheet so that the steel sheet can acquire the high strength, while hardness of the steel sheet is lowered in the surface layer of the steel sheet due to self annealing. Accordingly, the hot rolled steel sheet can acquire both the desired high strength and the desired low surface hardness.
The above-mentioned hot rolled steel sheet acquired by the manufacturing method of embodiments of the present invention is the thick-walled high-strength hot rolled steel sheet having excellent hydrogen induced cracking resistance which has the above-mentioned composition, has the single-phase structure (here, single phase structure meaning the structure where 98% or more of the structure is occupied by one phase) which is constituted of a bainitic ferrite phase or a bainite phase in the inside of the sheet, and has high strength of tensile strength: 520 MPa or more, and low surface layer hardness where hardness of the surface layer is 230HV or less. In this specification, “bainitic ferrite phase” also includes acicular ferrite, acicular ferrite. “Surface layer” means a region within 1 mm from the surface of the steel sheet in the sheet thickness direction.
Hereinafter, the present invention is explained in detail in conjunction with examples.

Example 1

Raw steel material (slab) s having the compositions shown in Tables 1 and 2 are subjected to hot rolling under hot rolling conditions shown in Tables 3 and 4. After hot rolling is completed, the hot rolled steel sheets are cooled under cooling conditions shown in Tables 3 and 4, and are coiled in a coil shape at coiling temperatures shown in Tables 3 and 4, and are turned into hot rolled steel sheets (steel strips) having sheet thicknesses shown in Tables 3 and 4.
Specimens are sampled from the obtained hot rolled steel sheet, and the observation of structure, a hardness test, a tensile test, an impact resistance test, circumferential weldability test, and a hydrogen induced cracking test are carried out with respect to these specimens, and surface hardness, tensile property, toughness, circumferential weldability and hydrogen induced cracking resistance are evaluated. The following test methods are used.

(1) Observation of Structure

Structure-observation-use specimens are sampled from the obtained hot rolled steel sheet, cross-sections of the specimens in the rolling direction are polished and etched. The cross section are observed for each specimen with ten visual fields or more at respective positions consisting of a surface layer and a sheet-thickness center position using an optical microscope (magnification: 1000 times), and a kind of the structure is identified and a structural fraction (volume %) are measured.

(2) Hardness Test

Hardness-measurement-use specimens are sampled from the obtained hot rolled steel sheet, a cross-section of the specimen in the rolling direction is polished. Hardness at positions 0.5 mm and 1 mm away from a surface of the specimen in the sheet thickness direction is measured at five points for each position. Arithmetic average values are obtained by calculating the obtained measured values and a higher value is set as surface layer hardness of the hot rolled steel sheet. Here, measurement of hardness is performed using a Vickers hardness meter with a testing force 0.5 kgf.

(3) Tensile Test

A tensile test is carried out with respect to the obtained hot rolled steel sheet such that the longitudinal direction of the specimen is aligned with the direction orthogonal to the rolling direction (C direction) in accordance with provisions of API-5L at a room temperature thus obtaining yield strength YS and tensile strength TS.

(4) Impact Resistance Test

V notch specimens are sampled from a sheet thickness center portion of the obtained hot rolled steel sheet such that the longitudinal direction of the specimen is aligned with the direction orthogonal to the rolling direction (C direction), and a Charpy impact test is carried out in accordance with provisions of JIS Z 2242 thus obtaining absorbed energy (J) at a test temperature of −80° C. The number of specimens is three and an arithmetic average of the obtained absorbed energy values is obtained, and the arithmetic average is set as an absorbed energy value E₋₈₀(J) of the steel sheet.

(5) Circumferential Weldability Test

The circumferential weldability is evaluated using a y-type weld cracking test. Test plates are sampled from the obtained hot rolled steel sheet, test welding is performed at a room temperature in accordance with the provisions of JIS Z 3158, and the presence or the non-presence of the occurrence of cracks is investigated. The circumferential weldability is evaluated by giving “X:bad” when cracks occur and “^o: good” when no cracks occur.

(6) Hydrogen Induced Cracking Test

HIC specimens (size: 100 mm×20 mm) are sampled from the obtained hot rolled steel sheet such that the longitudinal direction of the specimen is aligned with the rolling direction of the steel sheet, and the hydrogen induced cracking resistance is evaluated in accordance with the provisions of TM 0284 of NACE (National Association of Corrosion Engineers). A prescribed A solution is used as a test liquid. After immersing the specimens into the test liquid, CLR (%) is measured. It is determined that no hydrogen induced cracking occurs so that hydrogen induced cracking resistance is favorable when CLR is 0%. The presence or the non-presence of the occurrence of blisters is also investigated.
Obtained results are shown in Tables 5 and 6.
All examples of the present invention turned out to be high-strength hot rolled steel sheets having excellent hydrogen induced cracking resistance, wherein the hot rolled steel sheet has high strength of tensile strength: 520 MPa or more and low surface layer hardness of 230HV or less, and has a large sheet-thickness of 8.7 mm or more. On the other hand, comparison examples which do not fall within the scope of the present invention cannot secure desired properties necessary as a raw material for a high-strength electric-resistance welded steel pipe since the comparison examples cannot secure desired high strength, the comparison examples cannot acquire desired low surface layer hardness, the low temperature toughness is deteriorated, or the circumferential weldability is deteriorated, or hydrogen induced cracking resistance is deteriorated.

Example 2

Raw steel materials having the compositions shown in Tables 7 and 8 are subjected to hot rolling under hot rolling conditions shown in Tables 9 and 10. After hot rolling is completed, the hot rolled steel sheets are cooled under cooling conditions shown in Tables 9 and 10, and are coiled in a coil shape at coiling temperatures shown in Tables 9 and 10, and further, the hot rolled steel sheets are cooled under cooling conditions shown in Tables 9 and 10, are turned into hot rolled steel sheets (steel strips) having sheet thicknesses shown in Tables 9 and 10.
Specimens are sampled from the obtained hot rolled steel sheet, and the observation of structure, a hardness test, a tensile test, an impact resistance test, a circumferential weldability test, and a hydrogen induced cracking test are carried out with respect to these specimens, and a surface hardness, a tensile property, a toughness, a circumferential weldability and a hydrogen induced cracking resistance are evaluated. The following test methods are used.

(1) Observation of Structure

(2) Hardness Test

Hardness-measurement-use specimens are sampled from the obtained hot rolled steel sheet, a cross-section of the specimen in the rolling direction is polished. Hardness at positions 0.5 mm and 1.0 mm away from a surface of the specimen in the sheet thickness direction is measured at five points or more for each position. Arithmetic average values are obtained by calculating the obtained measured values as surface layer hardness of the hot rolled steel sheet. Here, measurement of hardness is performed using a Vickers hardness meter with a testing force 0.3 kgf (2.9N).

(3) Tensile Test

(4) Impact Resistance Test

V notch specimens are sampled from a sheet thickness center portion of the obtained hot rolled steel sheet such that the longitudinal direction of the specimen is aligned with the direction orthogonal to the rolling direction (C direction), and a Charpy impact test is carried out in accordance with provisions of JIS Z 2242 thus obtaining absorbed energy (J) at a test temperature of −80° C. The number of specimens is three and an arithmetic average of the obtained absorbed energy values is obtained, and the arithmetic average is set as an absorbed energy value vE₋₈₀(J) of the steel sheet.

(5) Circumferential Weldability Test

(6) Hydrogen Induced Cracking Test

HIC specimens (size: 100 mm×20 mm) are sampled from the obtained hot rolled steel sheet such that the longitudinal direction of the specimen is aligned with the rolling direction of the steel sheet, and the hydrogen induced cracking resistance is evaluated in accordance with the provisions of TM 0284 of NACE. A prescribed A solution is used as a test liquid. After immersing the specimens into the test liquid, CLR (%) is measured. It is determined that no hydrogen induced cracking occurs so that hydrogen induced cracking resistance is favorable when CLR is 0%. The presence or the non-presence of the occurrence of blisters is also investigated.
Obtained results are shown in Tables 11 and 12.
All examples of the present invention are turned out to be high-strength hot rolled steel sheets having excellent hydrogen induced cracking resistance, wherein the hot rolled steel sheet has high strength of tensile strength: 520 MPa or more and low surface layer hardness of 2301HV or less, possesses excellent circumferential weldability, and has a large sheet-thickness of 8.7 mm or more. On the other hand, comparison examples which do not fall within the scope of the present invention cannot secure desired properties necessary as a raw material for a high-strength electric-resistance welded steel pipe possessing excellent hydrogen induced cracking resistance of X65 grade or more since the comparison examples cannot secure desired high strength, the comparison examples cannot acquire desired low surface layer hardness, the low temperature toughness is deteriorated, or the circumferential weldability is deteriorated, or hydrogen induced cracking resistance is deteriorated.

TABLE 1

steel	chemical components (mass %)

No.	C	Si	Mn	P	S	Al	Nb	Ti	B	O	V, Mo, Cr, Ni, Cu

A	0.045	0.19	0.98	0.006	0.0004	0.039	0.050	0.012	0.0001	0.0020	V: 0.068, Cr: 0.23,
											Cu: 0.17, Ni: 0.16
B	0.022	0.21	1.04	0.008	0.0007	0.033	0.052	0.010	0.0002	0.0010	V: 0.070, Cr: 0.25,
											Cu: 0.16, Ni: 0.17
C	0.063	0.19	0.98	0.008	0.0006	0.034	0.049	0.009	0.0002	0.0011	Cu: 0.16, Ni: 0.16
D	0.041	0.21	0.53	0.007	0.0005	0.035	0.049	0.011	0.0002	0.0010	Mo: 0.20
E	0.020	0.21	1.79	0.008	0.0003	0.037	0.048	0.009	0.0002	0.0011	—
F	0.042	0.95	1.03	0.007	0.0004	0.035	0.050	0.010	0.0002	0.0017	—
G	0.041	0.22	1.07	0.006	0.0005	0.036	0.051	0.012	0.0004	0.0014	—
H	0.042	0.22	1.02	0.007	0.0003	0.033	0.001	0.010	0.0002	0.0011	—
I	0.049	0.21	1.04	0.005	0.0005	0.039	0.096	0.012	0.0002	0.0016	—
J	0.042	0.22	1.03	0.006	0.0004	0.034	0.048	0.011	0.0002	0.0014	—
K	0.048	0.20	0.99	0.005	0.0004	0.036	0.049	0.001	0.0002	0.0020	—
L	0.040	0.20	1.00	0.008	0.0005	0.034	0.065	0.045	0.0002	0.0010	—
M	0.040	0.20	1.00	0.008	0.0003	0.033	0.059	0.015	0.0002	0.0021	—
N	0.020	0.21	1.05	0.008	0.0005	0.030	0.091	0.048	0.0002	0.0016	—

chemical components (mass %)

	steel		left side value
	No.	Ca, REM, Mg	of formula (1)*	ACR**	Ceq***	Pcm****

	A	Ca: 0.0017	0.822	1.796	0.290	0.130
	B	Ca: 0.0019	1.636	1.683	0.281	0.112
	C	Ca: 0.0022	0.532	2.250	0.248	0.130
	D	Ca: 0.0022	0.866	2.774	0.169	0.089
	E	Ca: 0.0018	1.650	3.586	0.318	0.118
	F	Ca: 0.0019	0.833	2.348	0.214	0.126
	G	Ca: 0.0020	0.915	2.214	0.219	0.104
	H	Ca: 0.0018	0.250	3.586	0.212	0.101
	I	Ca: 0.0019	1.224	1.947	0.222	0.109
	J	Ca: 0.0110	0.833	17.492	0.214	0.102
	K	Ca: 0.0021	0.531	2.388	0.213	0.105
	L	Ca: 0.0021	1.938	2.635	0.207	0.098
	M	REM: 0.0033	1.113	5.390	0.207	0.098
	N	Ca: 0.0024	4.675	2.580	0.198	0.084

*left side value of formula (1) = (Ti + Nb/2)/C
**ACR = {Ca − O × (0.18 + 130Ca}/1.25S
***Ceq = C + Mn/6 + (Cr + Mo + V)/5 + (Cu + Ni)/15
****Pcm = C + Si/30 + (Mn + Cu + Cr)/20 + Ni/60 + Mo/15 + V/10 + 5B

TABLE 2

steel	chemical components (mass %)

No.	C	Si	Mn	P	S	Al	Nb	Ti	B	O	V, Mo, Cr, Ni, Cu

O	0.052	0.20	1.81	0.008	0.0004	0.034	0.059	0.034	0.0002	0.0017	Cr: 0.20
P	0.040	0.30	1.90	0.014	0.0036	0.035	0.059	0.028	0.0002	0.0020	V: 0.045,
											Cu: 0.28, Ni: 0.30
Q	0.091	0.20	1.21	0.008	0.0005	0.036	0.046	0.023	0.0002	0.0015	—
R	0.046	1.09	1.02	0.006	0.0004	0.034	0.046	0.010	0.0002	0.0014	—
S	0.043	0.22	1.05	0.007	0.0005	0.036	0.112	0.009	0.0002	0.0012	—
T	0.051	0.20	0.98	0.008	0.0004	0.036	0.046	0.011	0.0008	0.0011	—
U	0.048	0.19	0.99	0.007	0.0003	0.035	0.049	0.063	0.0002	0.0013	—
V	0.048	0.19	0.99	0.038	0.0003	0.035	0.049	0.063	0.0002	0.0013	—
W	0.048	0.19	0.99	0.007	0.0056	0.035	0.049	0.063	0.0002	0.0013	—
X	0.060	0.21	1.34	0.014	0.0021	0.041	0.018	0.012	0.0002	0.0011	V: 0.042
Y	0.043	0.02	1.09	0.008	0.0002	0.039	0.050	0.011	0.0002	0.0013	—
Z	0.041	0.02	0.27	0.008	0.0006	0.042	0.050	0.010	0.0002	0.0015	—
AA	0.041	0.30	1.02	0.007	0.0005	0.035	0.049	0.010	0.0002	0.0017	—
AB	0.020	0.21	1.62	0.008	0.0006	0.037	0.048	0.012	0.0002	0.0014	—

chemical components (mass %)

	steel		left side value
	No.	Ca, REM, Mg	of formula (1)*	ACR**	Ceq***	Pcm****

	O	Ca: 0.0022	1.221	2.816	0.394	0.160
	P	Ca: 0.0019	1.438	0.232	0.404	0.170
	Q	Ca: 0.0022	0.505	2.402	0.293	0.159
	R	Ca: 0.0021	0.717	2.932	0.216	0.134
	S	Ca: 0.0020	1.512	2.355	0.218	0.104
	T	Ca: 0.0023	0.667	3.546	0.214	0.111
	U	Ca: 0.0019	1.823	3.586	0.213	0.105
	V	Ca: 0.0019	1.823	3.586	0.213	0.105
	W	Ca: 0.0019	1.823	0.192	0.213	0.105
	X	Ca: 0.0021	0.350	0.610	0.292	0.139
	Y	—	0.837	−0.936	0.225	0.099
	Z	Ca: 0.0020	0.854	1.787	0.086	0.056
	AA	Mg: 0.0019	0.841	−0.490	0.211	0.103
	AB	Ca: 0.0014,	1.800	1.191	0.290	0.109
		Mg: 0.0011

*left side value of formula (1) = (Ti + Nb/2)/C
**ACR = {Ca − O × (0.18 + 130Ca}/1.25S
***Ceq = C + Mn/6 + (Cr + Mo + V)/5 + (Cu + Ni)/15
****Pcm = C + Si/30 + (Mn + Cu + Cr)/20 + Ni/60 + Mo/15 + V/10 + 5B

TABLE 3

	hot rolling condition	second

cumulative

first cooling step

cooling

			reduction rate	finish rolling	average	cooling stop	step
steel		heating	at 1000 ° C.	completion	surface	surface	air cooling
sheet	steel	temperature	or below	temperature	cooling rate	temperature	time
No.	No.	(° C.)	(%)	(° C.)	(° C./s)	(° C.)	(s)

1	A	1200	60	805	190	350	3.0
2	A	1150	60	820	320	135	1.5
3	A	1250	60	815	150	440	4.5
4	A	1100	60	780	75	620	2.5
5	A	1200	60	770	220	320	—
6	A	1250	60	800	240	360	1.5
7	A	1250	60	805	230	415	5.5
8	A	1200	60	795	290	370	1.5
9	A	1150	60	800	120	605	1.5
10	A	1200	60	790	250	335	2.0
11	A	1150	60	790	220	385	3.5
12	B	1200	60	785	190	400	4.0
13	C	1150	60	780	360	220	3.5
14	D	1250	60	815	200	410	3.0
15	E	1250	60	820	240	375	3.0
16	F	1150	60	800	190	415	3.0
17	G	1200	60	815	230	370	3.0
18	H	1150	60	805	190	405	3.0
19	I	1250	60	780	260	360	3.0

third cooling step

		average
		cooling rate
		at center of		coiling
	steel	sheet	cooling stop	coiling	sheet
	sheet	thickness	temperature*	temperature	thickness
	No.	(° C./s)	(° C.)	(° C.)	(mm)	remarks

	1	43	540	525	15.9	present invention example
	2	6	460	440	19.1	comparison example
	3	29	640	610	19.1	comparison example
	4	42	485	465	15.9	comparison example
	5	63	515	495	12.7	comparison example
	6	13	470	450	25.4	present invention example
	7	23	535	520	20.6	present invention example
	8	7	590	575	19.1	comparison example
	9	44	530	520	15.9	comparison example
	10	43	220	205	15.9	comparison example
	11	66	520	505	12.7	present invention example
	12	28	510	495	19.1	present invention example
	13	29	425	410	19.1	present invention example
	14	43	515	500	15.9	present invention example
	15	20	485	465	19.1	present invention example
	16	43	450	430	15.9	present invention example
	17	64	475	460	12.7	present invention example
	18	42	505	490	15.9	present invention example
	19	30	565	545	19.1	present invention example

*temperature at the center position of sheet thickness

TABLE 4

	hot rolling condition	second

cumulative

first cooling step

cooling

			reduction rate	finish rolling	average	cooling stop	step
steel		heating	at 1000 ° C.	completion	surface	surface	air cooling
sheet	steel	temperature	or below	temperature	cooling rate	temperature	time
No.	No.	(° C.)	(%)	(° C.)	(° C./s)	(° C.)	(s)

20	J	1200	60	770	290	345	3.0
21	K	1200	60	790	290	455	3.0
22	L	1200	60	800	250	400	3.0
23	M	1150	60	815	180	405	3.0
24	N	1200	60	805	190	365	3.0
25	O	1200	60	780	260	320	3.0
26	P	1250	60	820	190	340	3.0
27	Q	1200	60	815	240	345	3.0
28	R	1200	60	780	180	360	3.0
29	S	1150	60	805	200	345	3.0
30	T	1150	60	810	230	365	3.0
31	U	1200	60	795	260	325	3.0
32	V	1150	60	815	170	405	3.0
33	W	1200	60	820	190	410	3.0
34	X	1120	60	840	80	675	3.0
35	Y	1200	60	800	210	440	3.0
36	Z	1200	60	815	230	470	3.0
37	AA	1200	60	800	170	410	3.0
38	AB	1200	60	820	240	380	3.0

third cooling step

		average
		cooling rate
		at center of		coiling
	steel	sheet	cooling stop	coiling	sheet
	sheet	thickness	temperature*	temperature	thickness
	No.	(° C./s)	(° C.)	(° C.)	(mm)	remarks

	20	43	495	475	15.9	comparison example
	21	44	515	495	15.9	present invention example
	22	42	530	505	15.9	present invention example
	23	44	510	485	15.9	present invention example
	24	43	500	480	15.9	comparison example
	25	41	535	510	15.9	comparison example
	26	44	495	475	15.9	comparison example
	27	43	520	500	15.9	comparison example
	28	44	495	470	15.9	comparison example
	29	45	515	490	15.9	comparison example
	30	41	540	515	15.9	comparison example
	31	41	530	505	15.9	comparison example
	32	42	505	480	15.9	comparison example
	33	45	520	500	15.9	comparison example
	34	12	600	570	19.1	comparison example
	35	40	510	510	15.9	present invention example
	36	42	535	490	15.9	comparison example
	37	43	450	420	15.9	present invention example
	38	20	480	450	19.1	present invention example

*temperature at the center position of sheet thickness

TABLE 5

	structure

center of

hardness

HIC resistance

			sheet	surface	tensile	tough-	circum-		presence or
steel		surface layer	thickness	layer	strength	ness	ferential		no presence

sheet	steel	kind*; fraction	kind*; fraction	hardness	YS	TS	vE₋₈₀	weld-	CLR	of occurrence
No.	No.	(area %)	(area %)	HV	(MPa)	(MPa)	(J)	ability	(%)	of blister	remarks

1	A	M: 60, BF: 40	BF: 100	206	517	558	229	◯	0	no presence	present invention
											example
2	A	M: 65, BF: 35	F: 80, P: 20	243	512	569	55	◯	10	presence	comparison example
3	A	M: 80, BF: 20	F: 85, P: 15	234	516	578	111	◯	10	no presence	comparison example
4	A	M: 5, BF: 95	BF: 100	252	521	587	116	◯	5	presence	comparison example
5	A	M: 80, BF: 20	BF: 100	243	522	588	235	◯	5	presence	comparison example
6	A	M: 65, BF: 35	BF: 100	208	513	561	264	◯	0	no presence	present invention
											example
7	A	M: 70, BF: 30	BF: 100	206	509	567	270	◯	0	no presence	present invention
											example
8	A	M: 80, BF: 20	F: 85, P: 15	235	524	578	49	◯	5	no presence	comparison example
9	A	M: 70, BF: 30	BF: 100	254	526	575	97	◯	10	presence	comparison example
10	A	M: 5, BF: 95	BF: 100	261	519	574	265	◯	10	presence	comparison example
11	A	M: 55, BF: 45	BF: 100	196	524	581	245	◯	0	no presence	present invention
											example
12	B	M: 60, BF: 40	BF: 100	203	531	621	268	◯	0	no presence	present invention
											example
13	C	M: 60, BF: 40	BF: 100	218	519	599	249	◯	0	no presence	present invention
											example
14	D	M: 60, BF: 40	BF: 100	206	516	592	204	◯	0	no presence	present invention
											example
15	E	M: 65, BF: 35	BF: 100	211	541	589	199	◯	0	no presence	present invention
											example
16	F	M: 60, BF: 40	BF: 100	197	502	539	274	◯	0	no presence	present invention
											example
17	G	M: 60, BF: 40	BF: 100	213	521	574	262	◯	0	no presence	present invention
											example
18	H	M: 55, BF: 35	BF: 100	206	530	602	209	◯	0	no presence	present invention
											example
19	I	M: 70, BF: 30	BF: 100	215	563	611	299	◯	0	no presence	present invention
											example

*BF: bainitic ferrite, B: bainite, M: martensite, F: ferrite, P: pearlite

TABLE 6

	structure

center of

HIC resistance

			sheet	hardness	tensile	tough-	circum-		presence or
steel		surface layer	thickness	surface layer	strength	ness	ferential		no presence

20	J	M: 70, BF: 30	BF: 100	246	527	598	8	◯	10	presence	comparison example
21	K	M: 70, BF: 30	BF: 100	218	504	562	244	◯	0	no presence	present invention
											example
22	L	M: 65, BF: 35	BF: 100	202	563	629	213	◯	0	no presence	present invention
											example
23	M	M: 70, BF: 30	BF: 100	216	514	587	264	◯	0	no presence	present invention
											example
24	N	M: 60, BF: 40	BF: 100	182	453	513	202	X	5	no presence	comparison example
25	O	M: 75, BF: 25	BF: 100	261	573	647	10	X	10	presence	comparison example
26	P	M: 70, BF: 30	BF: 100	237	548	625	226	◯	10	no presence	comparison example
27	Q	M: 65, BF: 35	BF: 100	243	587	675	26	X	15	presence	comparison example
28	R	M: 90, BF: 10	BF: 100	237	541	592	11	◯	5	no presence	comparison example
29	S	M: 60, BF: 40	BF: 100	218	561	634	22	X	10	no presence	comparison example
30	T	M: 65, BF: 35	BF: 100	223	527	598	29	X	10	no presence	comparison example
31	U	M: 70, BF: 30	BF: 100	210	574	652	33	◯	5	no presence	comparison example
32	V	M: 65, BF: 35	BF: 100	241	541	593	17	X	10	presence	comparison example
33	W	M: 70, BF: 30	BF: 100	228	513	576	24	◯	15	no presence	comparison example
34	X	M: 75, BF: 25	BF: 100	251	508	661	12	◯	10	no presence	comparison example
35	Y	BF: 100	BF: 100	219	530	599	198	◯	0	no presence	present invention
											example
36	Z	M: 70, BF: 30	BF: 100	198	431	482	219	◯	5	no presence	comparison example
37	AA	M: 60, BF: 40	BF: 100	195	505	542	271	◯	0	no presence	present invention
											example
38	AB	M: 70, BF: 30	BF: 100	209	528	575	198	◯	0	no presence	present invention
											example

*BF: bainitic ferrite, B: bainite, M: martensite, F: ferrite, P: pearlite

TABLE 7

steel	chemical components (mass %)

No.	C	Si	Mn	P	S	Al	Nb	Ti	B	O	V, Mo, Cr, Ni, Cu

A	0.049	0.20	0.99	0.006	0.0003	0.040	0.050	0.010	0.0001	0.0019	V: 0.071, Cr: 0.23,
											Cu: 0.16, Ni: 0.17
B	0.023	0.19	1.03	0.007	0.0006	0.035	0.051	0.013	0.0002	0.0011	V: 0.068, Cr: 0.24,
											Cu: 0.16, Ni: 0.17
C	0.069	0.19	1.02	0.008	0.0005	0.036	0.053	0.008	0.0002	0.0016	Mo: 0.19,
											Cu: 0.17, Ni: 0.16
D	0.040	0.21	0.57	0.006	0.0006	0.059	0.047	0.012	0.0002	0.0017	—
E	0.052	0.20	1.39	0.007	0.0004	0.033	0.049	0.011	0.0002	0.0011	—
F	0.042	0.97	1.04	0.007	0.0003	0.035	0.052	0.009	0.0002	0.0013	—
G	0.039	0.21	0.98	0.008	0.0004	0.037	0.050	0.010	0.0004	0.0015	—
H	0.040	0.20	0.99	0.006	0.0004	0.031	0.031	0.009	0.0002	0.0013	—
I	0.056	0.21	1.06	0.006	0.0004	0.037	0.097	0.008	0.0002	0.0018	—
J	0.043	0.23	1.01	0.006	0.0005	0.036	0.046	0.010	0.0002	0.0017	—
K	0.048	0.20	1.07	0.007	0.0004	0.034	0.050	0.013	0.0002	0.0021	—
L	0.042	0.19	1.01	0.006	0.0005	0.038	0.063	0.012	0.0002	0.0016	—
M	0.041	0.19	1.02	0.007	0.0003	0.034	0.060	0.014	0.0002	0.0022	—

chemical components (mass %)

	steel		left side value
	No.	Ca, REM, Mg	of formula (1)*	ACR**	Ceq***	Pcm****

	A	Ca: 0.0018	0.714	2.702	0.296	0.135
	B	Ca: 0.0020	1.674	2.021	0.278	0.110
	C	Ca: 0.0022	0.500	2.327	0.299	0.138
	D	Ca: 0.0021	0.888	1.773	0.135	0.076
	E	Ca: 0.0017	0.683	2.518	0.284	0.128
	F	Ca: 0.0019	0.833	3.586	0.215	0.126
	G	Ca: 0.0019	0.897	2.290	0.202	0.095
	H	Ca: 0.0018	0.250	2.524	0.205	0.096
	I	Ca: 0.0018	1.009	2.110	0.233	0.116
	J	Ca: 0.0111	0.767	12.847	0.211	0.101
	K	Ca: 0.0020	0.792	2.152	0.226	0.108
	L	Ca: 0.0021	1.036	2.200	0.210	0.099
	M	REM: 0.0031	1.073	4.846	0.211	0.099

*left side value of formula (1) = (Ti + Nb/2)/C
**ACR = {Ca − O((0.18 + 130Ca}/1.25S
***Ceq = C + Mn/6 + (Cr + Mo + V)/5 + (Cu + Ni)/15
****Pcm = C + Si/30 + (Mn + Cu + Cr)/20 + Ni/60 + Mo/15 + V/10 + 5B

TABLE 8

steel	chemical components (mass %)

No.	C	Si	Mn	P	S	Al	Nb	Ti	B	O	V, Mo, Cr, Ni, Cu

N	0.021	0.20	1.06	0.007	0.0004	0.034	0.092	0.049	0.0002	0.0014	—
O	0.054	0.20	1.82	0.007	0.0003	0.036	0.061	0.036	0.0002	0.0019	Cr: 0.20
P	0.041	0.31	1.93	0.016	0.0037	0.037	0.058	0.030	0.0002	0.0021	V: 0.043,
											Cu: 0.28, Ni: 0.30
Q	0.089	0.20	1.23	0.006	0.0004	0.038	0.047	0.025	0.0002	0.0016	—
R	0.044	1.09	1.01	0.007	0.0003	0.036	0.048	0.011	0.0002	0.0015	—
S	0.042	0.23	1.03	0.008	0.0004	0.034	0.109	0.011	0.0002	0.0013	—
T	0.049	0.19	0.99	0.006	0.0005	0.036	0.048	0.009	0.0007	0.0010	—
U	0.046	0.18	1.01	0.007	0.0004	0.035	0.051	0.067	0.0002	0.0016	—
V	0.047	0.19	0.99	0.041	0.0004	0.037	0.053	0.012	0.0002	0.0015	—
W	0.048	0.20	0.96	0.007	0.0050	0.033	0.048	0.009	0.0002	0.0013	—
X	0.043	0.02	1.09	0.008	0.0002	0.039	0.050	0.011	0.0002	0.0013	—
Y	0.041	0.30	1.02	0.007	0.0005	0.035	0.049	0.010	0.0002	0.0017	—
Z	0.020	0.21	1.62	0.008	0.0006	0.037	0.048	0.012	0.0002	0.0014	—

chemical components (mass %)

	steel		left side value
	No.	Ca, REM, Mg	of formula (1)*	ACR**	Ceq***	Pcm****

	N	Ca: 0.0023	4.524	3.259	0.199	0.082
	O	Ca: 0.0023	1.231	3.706	0.397	0.162
	P	Ca: 0.0017	1.439	0.185	0.410	0.171
	Q	Ca: 0.0023	0.545	3.067	0.294	0.157
	R	Ca: 0.0021	0.795	3.788	0.212	0.131
	S	Ca: 0.0020	1.560	2.856	0.214	0.101
	T	Ca: 0.0021	0.673	2.635	0.214	0.105
	U	Ca: 0.0016	2.011	1.958	0.214	0.103
	V	Ca: 0.0014	0.819	1.714	0.212	0.103
	W	Ca: 0.0017	0.688	0.181	0.208	0.103
	X	—	0.837	−0.936	0.225	0.099
	Y	Mg: 0.0019	0.841	−0.490	0.211	0.103
	Z	Ca: 0.0014,	1.800	1.191	0.290	0.109
		Mg: 0.0011

*left side value of formula (1) = (Ti + Nb/2)/C
**ACR = {Ca − O((0.18 + 130Ca}/1.25S
***Ceq = C + Mn/6 + (Cr + Mo + V)/5 + (Cu + Ni)/15
****Pcm = C + Si/30 + (Mn + Cu + Cr)/20 + Ni/60 + Mo/15 + V/10 + 5B

TABLE 9

	hot rolling condition	first cooling step

			cumulative		martensite
			reduction	finish rolling	formation	average	cooling stop
steel		heating	rate at	completion	critical	surface	surface
sheet	steel	temperature	1000 ° C. or	temperature	cooling rate	cooling rate	temperature	Ar₃**	Ms(° C.)***
No	No.	(° C.)	below (%)	(° C.)	(° C./s)	(° C./s)	(° C.)	((C.)	((C.)

1	A	1200	60	800	350	200	510	800	498
2	A	1200	60	815	350	315	515	800	498
3	A	1150	60	820	350	100	565	800	498
4	A	1200	60	795	350	15	590	800	498
5	A	1200	60	780	350	550	520	800	498
6	A	1250	60	805	350	220	515	800	498
7	A	1150	60	810	350	180	500	800	498
8	A	1150	60	810	350	190	505	800	498
9	A	1250	60	805	350	260	520	800	498
10	A	1200	60	805	350	270	85	800	498
11	A	1250	60	795	350	260	515	800	498
12	A	1200	60	785	350	240	530	800	498
13	B	1150	60	790	500	180	520	804	509
14	C	1200	60	785	300	280	500	780	487
15	D	1200	60	815	400	260	535	852	523
16	E	1200	60	805	350	180	505	783	490
17	F	1150	60	800	400	230	520	814	507
18	G	1250	60	810	400	240	535	820	510
19	H	1200	60	815	400	180	520	818	509
20	I	1250	60	795	300	250	520	808	499

second cooling step

average

cooling

third cooling step

			rate at			keep time
		air	center of			between
	steel	cooling	sheet	cooling stop	coiling	350 and
	sheet	time	thickness	temperature*	temperature	600 ° C.
	No	(s)	((C./s)	((C.)	((C.)	(min)	remarks

	1	0.3	55	540	525	30 or more	present invention example
	2	0.3	24	460	440	30 or more	present invention example
	3	0.3	27	640	610	30 or more	comparison example
	4	0.3	56	485	465	30 or more	comparison example
	5	0.3	84	515	495	30 or more	comparison example
	6	0.3	54	470	455	30 or more	present invention example
	7	0.3	23	320	300	0	comparison example
	8	0.3	53	530	510	30 or more	present invention example
	9	0.3	21	590	575	30 or more	present invention example
	10	0.3	57	530	520	30 or more	comparison example
	11	0.3	21	560	550	30 or more	present invention example
	12	0.3	87	520	505	30 or more	present invention example
	13	0.3	29	510	495	30 or more	present invention example
	14	0.3	27	425	410	30 or more	present invention example
	15	0.3	54	515	500	30 or more	present invention example
	16	0.3	27	485	465	30 or more	present invention example
	17	0.3	60	450	430	30 or more	present invention example
	18	0.3	84	475	460	30 or more	present invention example
	19	0.3	59	505	490	30 or more	present invention example
	20	0.3	31	565	545	30 or more	present invention example

*temperature at the center position of sheet thickness
**value calculated using Ar₃(? C.) = 910-310C—80Mn—20Cu—15Cr—55Ni—80Mo
***value calculated using Ms(? C.) = 561-474C—33Mn—17Ni—17Cr—21Mo

TABLE 10

	hot rolling condition	first cooling step

			cumulative		martensite
			reduction	finish rolling	formation	average	cooling stop
steel		heating	rate at	completion	critical	surface	surface
sheet	steel	temperature	1000 ° C. or	temperature	cooling rate	cooling rate	temperature	Ar₃**	Ms(° C.)***
No	No.	((C.)	below (%)	((C.)	((C./s)	((C./s)	((C.)	((C.)	((C.)

21	J	1250	60	790	300	270	530	816	507
22	K	1150	60	785	350	240	520	810	503
23	L	1200	60	805	300	260	535	816	508
24	M	1200	60	805	300	200	540	816	508
25	N	1150	60	815	500	270	530	819	516
26	O	1250	60	795	400	280	515	745	472
27	P	1250	60	790	300	240	520	721	472
28	Q	1150	60	800	150	260	500	784	478
29	R	1200	60	785	350	270	520	816	507
30	S	1150	60	800	300	260	515	815	507
31	T	1200	60	805	350	290	520	816	505
32	U	1250	60	795	350	190	530	815	506
33	V	1200	60	780	350	260	520	816	506
34	W	1150	60	790	350	270	515	818	507
35	X	1200	60	800	350	240	520	811	502
36	Y	1150	60	800	400	220	520	813	508
37	Z	1200	60	805	350	185	510	782	488

second cooling step

average

cooling

third cooling step

			rate at			keep time
		air	center of			between
	steel	cooling	sheet	cooling stop	coiling	350 and
	sheet	time	thickness	temperature*	temperature	600 ° C.
	No	(s)	((C./s)	((C.)	((C.)	(min)	remarks

	21	0.3	58	495	475	30 or more	comparison example
	22	0.3	54	515	495	30 or more	present invention example
	23	0.3	55	530	505	30 or more	present invention example
	24	0.3	53	555	520	30 or more	present invention example
	25	0.3	53	500	480	30 or more	comparison example
	26	0.3	55	535	510	30 or more	comparison example
	27	0.3	61	495	475	30 or more	comparison example
	28	0.3	57	520	500	30 or more	comparison example
	29	0.3	59	495	470	30 or more	comparison example
	30	0.3	53	515	490	30 or more	comparison example
	31	0.3	50	540	515	30 or more	comparison example
	32	0.3	60	530	505	30 or more	comparison example
	33	0.3	53	505	480	30 or more	comparison example
	34	0.3	58	520	500	30 or more	comparison example
	35	0.3	55	510	490	30 or more	present invention example
	36	0.3	58	450	430	30 or more	present invention example
	37	0.3	26	480	460	30 or more	present invention example

*temperature at the center position of sheet thickness
**value calculated using Ar₃(? C.) = 910-310C—80Mn—20Cu—15Cr—55Ni—80Mo
***value calculated using Ms(? C.) = 561-474C—33Mn—17Ni—17Cr—21Mo

TABLE 11

	structure

center of

hardness

HIC resistance

		sheet		sheet	surface	tensile	tough-	circum-		presence or
steel		thick-	surface layer	thickness	layer	strength	ness	ferential		no presence

sheet

steel

ness

kind*; fraction

hardness

YS

TS

vE-8

weld-

CLR

of occurrence

No.

(mm)

(area %)

HV

(MPa)

(J)

ability

(%)

of blister

remarks

1	A	15.9	BF: 100	BF: 100	212	508	579	268	◯	0	no presence	present invention
												example
2	A	19.1	BF: 100	BF: 100	223	501	574	224	◯	0	no presence	present invention
												example
3	A	19.1	BF: 95, P: 5	F: 90, P: 10	234	498	589	63	◯	15	no presence	comparison example
4	A	15.9	F: 85, P: 15	F: 80, P: 20	256	503	579	22	◯	10	presence	comparison example
5	A	12.7	M: 75,	BF: 95, P: 5	278	511	586	20	◯	15	presence	comparison example
6	A	15.9	BF: 100	BF: 100	214	490	568	255	◯	0	no presence	present invention
												example
7	A	20.6	BF: 100	BF: 100	209	459	516	226	◯	10	no presence	comparison example
8	A	15.9	BF: 100	BF: 100	216	502	576	215	◯	0	no presence	present invention
												example
9	A	20.6	BF: 100	BF: 100	213	507	584	215	◯	0	no presence	present invention
												example
10	A	15.9	M: 70, BF: 30	BF: 95, M: 5	264	498	581	56	◯	15	presence	comparison example
11	A	33.4	BF: 100	BF: 100	199	501	590	246	◯	0	no presence	present invention
												example
12	A	12.7	BF: 100	BF: 100	203	497	596	261	◯	0	no presence	present invention
												example
13	B	19.1	BF: 100	BF: 100	204	512	634	237	◯	0	no presence	present invention
												example
14	C	19.1	BF: 100	BF: 100	213	501	608	241	◯	0	no presence	present invention
												example
15	D	15.9	BF: 100	BF: 100	196	497	598	224	◯	0	no presence	present invention
												example
16	E	19.1	BF: 100	BF: 100	206	522	607	264	◯	0	no presence	present invention
												example
17	F	15.9	BF: 100	BF: 100	207	496	561	238	◯	0	no presence	present invention
												example
18	G	12.7	BF: 100	BF: 100	218	514	598	251	◯	0	no presence	present invention
												example
19	H	15.9	BF: 100	BF: 100	194	517	617	224	◯	0	no presence	present invention
												example
20	I	19.1	BF: 100	BF: 100	209	562	629	274	◯	0	no presence	present invention
												example

*BF: bainitic ferrite, B: bainite, M: martensite, F: ferrite, P: pearlite

TABLE 12

	structure

center of

hardness

HIC resistance

sheet

steel

ness

kind*; fraction

hardness

YS

TS

vE-8

weld-

CLR

of occurrence

No.

(mm)

(area %)

HV

(MPa)

(J)

ability

(%)

of blister

remarks

21	J	15.9	BF: 95, M: 5	BF: 100	247	517	609	11	◯	15	presence	comparison example
22	K	15.9	BF: 100	BF: 100	206	494	574	241	◯	0	no presence	present invention
												example
23	L	15.9	BF: 100	BF: 100	197	559	638	237	◯	0	no presence	present invention
												example
24	M	15.9	BF: 100	BF: 100	215	513	584	246	◯	0	no presence	present invention
												example
25	N	15.9	F: 90, P: 10	F: 75, P: 25	168	432	514	222	X	15	no presence	comparison example
26	O	15.9	BF: 90, M: 10	BF: 95, M: 5	263	569	633	17	X	15	presence	comparison example
27	P	15.9	BF: 95, M: 5	BF: 100	240	516	631	217	◯	5	presence	comparison example
28	Q	15.9	M: 60, BF: 40	F: 90, P: 10	256	574	684	29	X	10	presence	comparison example
29	R	15.9	F: 95, P: 5	F: 80, P: 20	239	539	608	26	◯	5	no presence	comparison example
30	S	15.9	BF: 100	BF: 100	217	557	637	37	X	15	no presence	comparison example
31	T	15.9	BF: 90, M: 10	BF: 100	249	508	607	17	X	5	presence	comparison example
32	U	15.9	BF: 100	BF: 100	221	569	664	50	◯	10	no presence	comparison example
33	V	15.9	BF: 100	BF: 100	251	539	609	27	X	10	presence	comparison example
34	W	15.9	BF: 100	BF: 100	237	522	597	28	◯	20	no presence	comparison example
35	X	15.9	BF: 100	BF: 100	203	521	580	240	◯	0	no presence	present invention
												example
36	Y	15.9	BF: 100	BF: 100	206	498	566	235	◯	0	no presence	present invention
												example
37	Z	19.1	BF: 100	BF: 100	204	531	608	262	◯	0	no presence	present invention
												example

*BF: bainitic ferrite, B: bainite, M: martensite, F: ferrite, P: pearlite

Claims

1. A thick-walled high-strength hot rolled steel sheet having a composition which contains by mass % 0.02 to 0.08% C, 1.0% or less Si, 0.50 to 1.85% Mn, 0.03% or less P, 0.005% or less S, 0.1% or less Al, 0.03 to 0.10% Nb, 0.001 to 0.05% Ti, 0.0005% or less B, and Fe and unavoidable impurities as a balance, wherein the steel sheet contains Nb, Ti and C in such a manner that a following formula (1) is satisfied, the steel sheet has the structure formed of a bainitic ferrite phase or a bainite phase, and surface layer hardness is 230HV or less in terms of Vickers hardness, wherein

(Ti+Nb/2)/C<4 Ti, Nb, C: contents of respective elements (mass %).

2. The thick-walled high-strength hot rolled steel sheet according to claim 1, wherein the composition further contains by mass % one or two kinds or more selected from a group consisting of 0.5% or less V, 1.0% or less Mo, 1.0% or less Cr, 4.0% or less Ni, and 2.0% or less Cu in addition to the composition.

3. The thick-walled high-strength hot rolled steel sheet according to claim 1, wherein the composition further contains by mass % one or two kinds or more selected from a group consisting of 0.010% or less Ca, 0.02% or less REM, and 0.003% or less Mg in addition to the composition.

4. The thick-walled high-strength hot rolled steel sheet according to claim 1, wherein the composition further satisfies at least one of a condition that Ceq defined by a following formula (2) is 0.32% or less and a condition that Pcm defined by a following formula (3) is 0.13% or less, wherein

Ceq=C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15 (2)

Pcm=C+Si/30+(Mn+Cu+Cr)/20+Ni/60+Mo/15+V/10+5B (3)

Here, C, Si, Mn, Cr, Mo, V, Cu, Ni, B: contents of respective elements (mass %).

5. A method of manufacturing a thick-walled high-strength hot rolled steel sheet having surface layer hardness of 230HV or less in terms of Vickers hardness, wherein in manufacturing a hot rolled steel sheet by applying hot rolling consisting of rough rolling and finish rolling to a raw steel material having the composition according to claim 1, after the finish rolling is finished, a first cooling step in which the hot rolled steel sheet is cooled by accelerated cooling at an average surface cooling rate of 30° C./s or more until a surface temperature becomes 500° C. or below, a second cooling step in which the hot rolled steel sheet is cooled by air cooling for 10s or less after the first cooling step is finished, and a third cooling step in which the hot rolled steel sheet is cooled by accelerated cooling to a temperature which falls within a temperature range from 350° C. or above to a temperature below 600° C. at the center of a sheet-thickness at an average cooling rate of 10° C./s or more at the center of the sheet-thickness are applied to the hot rolled steel sheet, and the hot rolled steel sheet is coiled in a coil shape after the third cooling step is finished.

6. The method of manufacturing a thick-walled high-strength hot rolled steel sheet according to claim 5, wherein the accelerated cooling in the third cooling step is cooling performed at a heat flow rate of 1.5 Gcal/m²hr or more in entire surface nuclear boiling.

7. The method of manufacturing a thick-walled high-strength hot rolled steel sheet according to claim 5, wherein the composition further contains by mass % one or two kinds or more selected from a group consisting of 0.5% or less V, 1.0% or less Mo, 1.0% or less Cr, 4.0% or less Ni, and 2.0% or less Cu in addition to the composition.

8. The method of manufacturing a thick-walled high-strength hot rolled steel sheet according to claim 5, wherein the composition further contains by mass % one or two kinds or more selected from a group consisting of 0.010% or less Ca, 0.02% or less REM, and 0.003% or less Mg in addition to the composition.

9. The method of manufacturing a thick-walled high-strength hot rolled steel sheet according to claim 5, wherein the composition further satisfies at least one of a condition that Ceq defined by a following formula (2) is 0.32% or less and a condition that Pcm defined by a following formula (3) is 0.13% or less, wherein

Ceq=C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15 (2)

Pcm=C+Si/30+(Mn+Cu+Cr)/20+Ni/60+Mo/15+V/10+5B (3)

10. A method of manufacturing a thick-walled high-strength hot rolled steel sheet having tensile strength of 520 MPa or more and a surface layer hardness of 230HV or less in terms of Vickers hardness, wherein in manufacturing a hot rolled steel sheet by applying hot rolling consisting of rough rolling and finish rolling to a raw steel material having the composition according to claim 1, after the finish rolling is finished, a first cooling step in which the hot rolled steel sheet is cooled by accelerated cooling at an average cooling rate of 20° C./s or more and less than a martensite formation critical cooling rate on a surface of the hot rolled steel sheet until a surface temperature becomes a temperature not more than an A_r3transformation temperature and not less than an Ms temperature, a second cooling step in which the hot rolled steel sheet is rapidly cooled to a temperature within a temperature range from 350° C. or above to a temperature below 600° C. at the center of a sheet-thickness after the first cooling step is finished, and a third cooling step in which, after the second cooling step is finished, the hot rolled steel sheet is coiled in a coil shape at a coiling temperature falling within a temperature range from 350° C. or above to a temperature below 600° C. in terms of a temperature at the center of sheet-thickness and, thereafter, a temperature of the hot rolled steel sheet at least at a position of ¼ sheet-thickness to ¾ sheet-thickness in a coil thickness direction is held or kept within a temperature range from 350° C. or above to a temperature below 600° C. for 30 min or more are sequentially applied to the hot rolled steel sheet.

11. The method of manufacturing a thick-walled high-strength hot rolled steel sheet according to claim 10, wherein the rapid cooling in the second cooling step is cooling at a heat flow rate of 1.0 Gcal/m²hr or more in entire surface nuclear boiling.

12. The method of manufacturing a thick-walled high-strength hot rolled steel sheet according to claim 10, wherein the composition further contains by mass % one or two kinds or more selected from a group consisting of 0.5% or less V, 1.0% or less Mo, 1.0% or less Cr, 4.0% or less Ni, and 2.0% or less Cu in addition to the composition.

13. The method of manufacturing a thick-walled high-strength hot rolled steel sheet according to claim 10, wherein the composition further contains by mass % one or two kinds selected from a group consisting of 0.010% or less Ca, 0.02% or less REM, 0.003% or less Mg in addition to the composition.

14. The method of manufacturing a thick-walled high-strength hot rolled steel sheet according to claim 10, wherein the composition further satisfies at least one of a condition that Ceq defined by a following formula (2) is 0.32% or less and a condition that Pcm defined by a following formula (3) is 0.13% or less, wherein

Ceq=C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15 (2)

Pcm=C+Si/30+(Mn+Cu+Cr)/20+Ni/60+Mo/15+V/10+5B (3)

C, Si, Mn, Cr, Mo, V, Cu, Ni, B: contents of respective elements (mass %).