WO2014041802A1

WO2014041802A1 - Hot-rolled steel sheet and method for manufacturing same

Info

Publication number: WO2014041802A1
Application number: PCT/JP2013/005388
Authority: WO
Inventors: 力上; 聡太後藤
Original assignee: Ｊｆｅスチール株式会社
Priority date: 2012-09-13
Filing date: 2013-09-11
Publication date: 2014-03-20
Also published as: JPWO2014041802A1; JP5605527B2; CN104619876B; KR101702794B1; EP2871254A1; EP2871254B1; IN2015DN00772A; US20150232970A1; BR112015005419A2; CN104619876A; EP2871254A4; KR20150038747A

Abstract

Provided is a low-yield-ratio, high-strength hot-rolled steel sheet having excellent low-temperature toughness and being appropriate as a steel pipe raw material. The present invention has a composition including 0.03-0.10% C, 0.01-0.50% Si, 1.4-2.2% Mn, no more than 0.025% P, no more than 0.005% S, 0.005-0.10% Al, 0.02-0.10% Nb, 0.001-0.030% Ti, 0.01-0.50% Mo, 0.01-0.50% Cr, and 0.01-0.50% Ni, Moeq preferably satisfying a range of 1.4-2.2%, and the inner layers have a structure that includes bainitic ferrite having an average grain size no larger than 10 µm as a main phase and massive martensite having a surface area ratio of 1.4-15% and an aspect ratio of less than 5.0 as a second phase, the surface layer comprising a tempered martensite phase or a tempered martensite phase and a tempered bainite phase.

Description

Hot-rolled steel sheet and manufacturing method thereof

The present invention relates to a low-yield-ratio high-strength hot-rolled steel sheet suitable as a material for spiral steel pipes or ERW steel pipes used for line pipes and a method for producing the same. In particular, it relates to ensuring a low yield ratio and excellent low temperature toughness while preventing a decrease in yield strength after pipe making.

In recent years, spiral steel pipes that are formed by spirally winding a steel sheet can be used to efficiently produce large-diameter steel pipes, and in recent years have come to be widely used as line pipes for transporting crude oil and natural gas. In particular, pipelines for long-distance transportation are required to have high transportation efficiency and have a high pressure, and there are many oil wells and gas wells in cold regions, and they often pass through cold regions. For this reason, the line pipe used is required to have high strength and high toughness. Furthermore, from the viewpoint of buckling resistance and earthquake resistance, the line pipe is required to have a low yield ratio. The yield ratio of the spiral steel pipe in the longitudinal direction of the pipe hardly changes depending on the pipe making, and almost coincides with that of the hot-rolled steel sheet. Therefore, in order to reduce the yield ratio of a line pipe made of spiral steel pipe, it is necessary to lower the yield ratio of the hot-rolled steel sheet as the material.
In response to such a demand, for example, Patent Document 1 describes a method of manufacturing a hot-rolled steel sheet for a low-yield ratio high-tensile line pipe excellent in low-temperature toughness. The technique described in Patent Document 1 contains, by weight, C: 0.03-0.12%, Si: 0.50% or less, Mn: 1.70% or less, Al: 0.070% or less, and Nb: 0.01-0.05%. , V: 0.01 to 0.02%, Ti: 0.01 to 0.20% of a steel slab containing at least one kind is heated to 1180 to 1300 ° C, then rough rolling finish temperature: 950 to 1050 ° C, finish rolling finish temperature : Hot rolled under conditions of 760 to 800 ° C, cooled at a cooling rate of 5 to 20 ° C / s, started air cooling until reaching 670 ° C, held for 5 to 20s, then 20 ° C / It is cooled at a cooling rate of s or higher and wound at a temperature of 500 ° C. or lower to form a hot rolled steel sheet. According to the technique described in Patent Document 1, the tensile strength of 60 kg / mm ² or more (590 MPa or higher) in yield ratio of 85% or less, fracture appearance transition temperature: hot-rolled steel sheet having a -60 ° C. or less of the high toughness It can be manufactured.
Patent Document 2 describes a method for producing a hot-rolled steel sheet for a high-strength, low-yield ratio pipe. The technology described in Patent Document 2 contains C: 0.02 to 0.12%, Si: 0.1 to 1.5%, Mn: 2.0% or less, Al: 0.01 to 0.10%, and Mo + Cr: 0.1 to 1.5% The steel to be heated is heated to 1000-1300 ° C, the hot rolling is finished in the range of 750-950 ° C, cooled to the coiling temperature at a cooling rate of 10-50 ° C / s, and in the range of 480-600 ° C. It is a manufacturing method of the hot-rolled steel plate wound up. According to the technique described in Patent Document 2, without quenching from the austenite temperature range, it is mainly composed of ferrite, has a martensite with an area ratio of 1 to 20%, has a yield ratio of 85% or less, In addition, it is said that a hot-rolled steel sheet with a small decrease in yield strength after pipe making can be obtained.
Patent Document 3 describes a method for producing a low yield ratio electric resistance welded steel pipe excellent in low temperature toughness. The technology described in Patent Document 3 includes, in mass%, C: 0.01 to 0.09%, Si: 0.50% or less, Mn: 2.5% or less, Al: 0.01 to 0.10%, Nb: 0.005 to 0.10% In addition, one or more of Mo: 0.5% or less, Cu: 0.5% or less, Ni: 0.5% or less, Cr: 0.5% or less, Mn, Si, P, Cr, Ni, Mo A slab with a composition containing Mneq that satisfies the content relation of 2.0 or more is hot-rolled, cooled to 500 to 650 ° C at a cooling rate of 5 ° C / s or more, and this temperature range. Then, the steel sheet is retained for 10 minutes or more and then cooled to a temperature of less than 500 ° C. to form a hot-rolled steel sheet. According to the technique described in Patent Document 3, it has a structure containing bainitic ferrite as a main phase and containing 3% or more martensite and, if necessary, 1% or more retained austenite, and has a fracture surface transition temperature of It is said that ERW steel pipes with excellent low temperature toughness and high plastic deformation absorption ability can be manufactured at -50 ° C or lower.
Patent Document 4 describes a low yield ratio high toughness thick steel plate. In the technique described in Patent Document 4, C: 0.03 to 0.15%, Si: 1.0% or less, Mn: 1.0 to 2.0%, Al: 0.005 to 0.060%, Ti: 0.008 to 0.030%, N: 0.0020 to 0.010% , O: Heated to a slab having a composition containing 0.010% or less, preferably 950 to 1300 ° C, and the reduction rate in the temperature range of (Ar3 transformation point + 100 ° C) to (Ar3 transformation point + 150 ° C) is 10% or more. After hot rolling at a finish rolling temperature of 800-700 ° C, accelerated cooling is started within -50 ° C from the finish rolling temperature, and up to 400-150 ° C at an average cooling rate of 5-50 ° C / s. After cooling with water, air-cooled steel sheets with a low yield ratio and high toughness having a mixed structure of ferrite with an average particle size of 10 to 50 μm and bainite with 1 to 20 area% of island martensite dispersed You can get. In addition, there is no mention about the shape (bar shape, lump shape: mentioned later) of island martensite.

JP 63-227715 A Japanese Patent Laid-Open No. 10-176239 JP 2006-299413 JP JP 2010-59472 A

However, in the technique described in Patent Document 1, since the cooling rate is large before and after air cooling, particularly after air cooling, it is necessary to quickly and appropriately control the cooling rate, the cooling stop temperature, and the like. In order to manufacture a steel plate, there is a problem that a large-scale cooling facility is required. Moreover, the hot-rolled steel sheet obtained by the technique described in Patent Document 1 has a problem that it has a structure mainly composed of soft polygonal ferrite and it is difficult to obtain a desired high strength.
Moreover, in the technique described in Patent Document 2, a decrease in yield strength after pipe forming is still recognized, and there is a problem that a recent increase in steel pipe strength cannot be satisfied.
In addition, the technique described in Patent Document 3 has a problem that it has not yet been able to stably secure excellent low-temperature toughness, which is a recent cold region specification, with a fracture surface transition temperature vTrs of −80 ° C. or lower. .
In addition, the thick steel plate obtained by the technique described in Patent Document 4 can only secure a toughness of about −30 to −41 ° C. at the fracture surface transition temperature vTrs at the latest. There is a problem that can not be dealt with.
In recent years, high strength and thick steel pipe materials have been demanded from the requirement of transporting crude oil and the like with high efficiency. However, there is a problem that the amount of alloying elements is increased for increasing the strength, and a rapid cooling process in the hot-rolled steel sheet manufacturing process is inevitably accompanied with the increase in thickness. Since a hot-rolled steel sheet is transported at a high speed through a limited length of a water-cooled zone and wound in a coil shape, it is necessary to perform strong cooling as the plate thickness increases. For this reason, there exists a problem that the surface hardness of a steel plate becomes higher than necessary.
In particular, for example, when manufacturing a hot-rolled steel sheet having a thickness of 10 mm or more, the finishing zone is fed at a high speed of 100 to 250 mpm, so that the cooling zone after the finish rolling is similarly fed at a high speed. Therefore, it is necessary to perform cooling having a large heat transfer coefficient as the plate thickness increases. For this reason, there is a problem that the surface hardness of the hot-rolled steel sheet becomes higher than necessary, and the surface of the hot-rolled steel sheet is hardened as compared with the inside of the plate thickness, and the uneven distribution is often increased. Such a non-uniform distribution of hardness also causes a problem that the steel pipe characteristics vary. Further, the nonuniformity in the surface hardness distribution is caused by the steel sheet surface staying in the transition boiling temperature region (boundary between film boiling and nucleate boiling) in the cooling process. In order to avoid this, it is necessary to prevent the surface temperature of the steel sheet from becoming 500 ° C or lower. However, if the plate is thick, the internal cooling rate will be too slow to form the desired inner layer structure. Can not be. On the other hand, by reducing the steel sheet surface temperature to a temperature range lower than the transition boiling region, the surface hardness can be made uniform, but the maximum hardness of the cross section exceeds 300 points at HV0.5. Due to this increase in hardness, not only the problem of the pipe shape after pipe making, but also the problems of the steel pipe characteristics and the inability to make pipes become obvious.
The present invention solves the problems of the prior art, and does not require complex heat treatment, and without extensive modification of equipment, and is suitable for steel pipe materials, particularly for spiral steel pipes. An object of the present invention is to provide a high yield hot-rolled steel sheet having a low yield ratio and excellent in low temperature toughness that can be prevented from lowering. In particular, an object is to provide a low yield ratio high strength hot-rolled steel sheet having excellent low-temperature toughness having a thickness of 8 mm or more (more preferably 10 mm or more) and 50 mm or less (more preferably 25 mm or less). The term “high strength” as used herein refers to the case where the yield strength in the 30-degree direction from the rolling direction is 480 MPa or more and the tensile strength in the sheet width direction is 600 MPa or more, and “excellent in low temperature toughness” When the fracture surface transition temperature vTrs of the Charpy impact test is -80 ° C or less, and "low yield ratio" indicates a continuous yield type stress-strain curve and the yield ratio is 85% or less, Each shall be said. The “steel plate” includes a steel plate and a steel strip.

In order to achieve the above-mentioned object, the present inventors diligently studied various factors affecting steel pipe strength after pipe making and steel pipe toughness. As a result, the decrease in strength due to pipe making is caused by the decrease in yield strength due to the Bauschinger effect on the inner surface of the tube where compressive stress acts and the disappearance of yield elongation on the outer surface side where tensile stress acts. I found out.
Therefore, as a result of further research, the inventors have made a structure in which the structure of the steel sheet has fine bainitic ferrite as a main phase, and hard massive martensite is finely dispersed in the bainitic ferrite. As a result, it was conceived that a steel pipe having a low yield ratio of 85% or less and further excellent toughness can be obtained after pipe making, in particular, after strength reduction after spiral pipe making. . With such a structure, the work hardening ability of the steel sheet, which is the steel pipe material, is improved, so that a sufficient increase in strength is obtained by work hardening on the pipe outer surface side during pipe making. It has been found that the strength reduction after the pipe can be suppressed and that the toughness is remarkably improved by finely dispersing the massive martensite.
In addition, in order to prevent a non-uniform increase in the surface hardness of the steel sheet, to make a steel pipe excellent in pipe shape after forming and having a uniform deformability, the surface structure of the steel sheet is tempered martensite phase single phase or tempered. It was also found that a mixed phase of martensite and tempered bainite is effective.
The present invention has been completed based on such findings and further studies. That is, the gist of the present invention is as follows.
(1) By mass%, C: 0.03 to 0.10%, Si: 0.01 to 0.50%, Mn: 1.4 to 2.2%, P: 0.025% or less, S: 0.005% or less, Al: 0.005 to 0.10%, Nb: 0.02 0.10%, Ti: 0.001 to 0.030%, Mo: 0.01 to 0.50%, Cr: 0.01 to 0.50%, Ni: 0.01 to 0.50%, the composition of the balance Fe and unavoidable impurities, Bainitic ferrite with an average particle size of 10 μm or less as the main phase, and the second phase is a structure containing massive martensite with an area ratio of 1.4 to 15% in area ratio: less than 5.0, and the surface layer is tempered martensite A hot-rolled steel sheet characterized by having a structure comprising a phase or a tempered martensite phase and a tempered bainite phase.
(2) In (1), the composition is expressed by mass%, and the following formula (1)
Moeq (%) = Mo + 0.36Cr + 0.77Mn + 0.07Ni (1)
(Where Mn, Ni, Cr, Mo: content of each element (mass%))
A hot-rolled steel sheet characterized by having a composition satisfying a Moeq defined in the range of 1.4 to 2.2%.
(3) In (1) or (2), in addition to the above composition, in addition to mass, Cu: 0.50% or less, V: 0.10% or less, B: 0.0005% or less A hot-rolled steel sheet containing more than seeds.
(4) A hot rolled steel sheet according to any one of (1) to (3), further containing Ca: 0.0005 to 0.0050% by mass% in addition to the above composition.
(5) The hot rolled steel sheet according to any one of (1) to (4), wherein the bulk martensite has a maximum size of 5.0 μm or less and an average of 0.5 to 3.0 μm.
(6) The hot rolled steel sheet according to any one of (1) to (5), wherein the hardness at a depth of 0.5 mm from the surface in the thickness direction is 95% or less of the maximum hardness in the thickness direction.
(7) When the steel material is subjected to a hot rolling process, a cooling process, and a winding process to obtain a hot rolled steel sheet, the steel material is, in mass%, C: 0.03-0.10%, Si: 0.01-0.50% , Mn: 1.4 to 2.2%, P: 0.025% or less, S: 0.005% or less, Al: 0.005 to 0.10%, Nb: 0.02 to 0.10%, Ti: 0.001 to 0.030%, Mo: 0.01 to 0.50%, Cr: A steel material having a composition comprising 0.01 to 0.50%, Ni: 0.01 to 0.50%, the balance being Fe and inevitable impurities, and the hot rolling step, heating the steel material to a heating temperature of 1050 to 1300 ° C, The heated steel material is subjected to rough rolling to form a sheet bar, and the sheet bar is subjected to a finish rolling at a temperature range of 930 ° C. or lower and finish rolling to be 50% or more to form a hot rolled steel sheet, The cooling process is started immediately after finishing rolling, and the surface temperature is equal to or lower than the martensite transformation start temperature (Ms point) at an average cooling rate of 100 ° C./s or higher. Primary cooling to a temperature of 2 ° C., secondary cooling in which the surface temperature stays at a temperature of 600 ° C. or higher for 1 s or more after the completion of the primary cooling, and the average thickness of the central portion after the secondary cooling is 5 to The tertiary cooling that cools to a cooling stop temperature in the temperature range of 600 to 450 ° C at a cooling rate of 30 ° C / s, and the average from the cooling stop temperature of the tertiary cooling to the coiling temperature at the center temperature of the plate thickness And cooling at a cooling rate of 2 ° C./s or less, or quaternary cooling in which the liquid is retained for 20 seconds or more in the temperature range from the cooling stop temperature of the tertiary cooling to the coiling temperature. A method for producing a hot-rolled steel sheet, characterized by a step of winding at a surface temperature and a winding temperature: 450 ° C. or higher.
(8) In (7), the composition is expressed by mass%, and the following formula (1)
Moeq (%) = Mo + 0.36Cr + 0.77Mn + 0.07Ni (1)
(Where Mn, Ni, Cr, Mo: content of each element (mass%))
A method for producing a hot-rolled steel sheet, characterized by having a composition satisfying a Moeq defined in the range of 1.4 to 2.2%.
(9) In (7) or (8), in addition to the above-mentioned composition, by mass%, one or two selected from Cu: 0.50% or less, V: 0.10% or less, B: 0.0005% or less The manufacturing method of the hot rolled sheet steel characterized by including a seed or more.
(10) The method for producing a hot-rolled steel sheet according to any one of (7) to (9), further comprising Ca: 0.0005 to 0.0050% by mass% in addition to the above composition.

According to the present invention, particularly suitable as a material for spiral steel pipes, there is little decrease in strength after pipe forming, there is no uneven distribution of surface hardness, cross-sectional hardness is also reduced, and pipe shape and uniformity during pipe forming Excellent deformability, yield strength in the direction of 30 degrees from the rolling direction is 480 MPa or more, tensile strength in the plate width direction is 600 MPa or more, fracture surface transition temperature vTrs of Charpy impact test is -80 ° C or less, and yield ratio A low yield ratio high strength hot-rolled steel sheet having an excellent low temperature toughness of 85% or less is obtained. And the low yield ratio high-strength hot-rolled steel sheet of this invention can be manufactured easily and cheaply, without performing special heat processing. As described above, the present invention has a remarkable industrial effect. In addition, according to the present invention, there is an effect that a line pipe laid by the reel barge method and an ERW steel pipe for a line pipe that requires earthquake resistance can be easily and inexpensively manufactured. Moreover, if the low-yield ratio high-strength hot-rolled steel sheet according to the present invention is used as a raw material, there is also an effect that a high-strength spiral steel pipe pile serving as a building member and a port member having excellent earthquake resistance can be manufactured. Moreover, since the spiral steel pipe using such a hot-rolled steel sheet has a low yield ratio in the longitudinal direction of the pipe, it has an effect that it can also be applied to high-value-added high-strength steel pipe piles.

It is explanatory drawing which shows typically the relationship between the production | generation of massive martensite, and the secondary cooling in the cooling after hot rolling.

First, the reasons for limiting the composition of the hot-rolled steel sheet of the present invention will be described. Hereinafter, unless otherwise specified, mass% is simply expressed as%.
C: 0.03-0.10%
C precipitates as a carbide and contributes to an increase in the strength of the steel sheet through precipitation strengthening. It is also an element that contributes to improving the toughness of the steel sheet through grain refinement. Further, C has an action of forming a solid solution in the steel, stabilizing austenite, and promoting the formation of untransformed austenite. In order to obtain these effects, a content of 0.03% or more is required. On the other hand, if the content exceeds 0.10%, the tendency to form coarse cementite at the grain boundaries becomes strong, and the toughness decreases. For this reason, C is limited to the range of 0.03-0.10%. Preferably, the content is 0.04 to 0.09%.
Si: 0.01-0.50%
Si contributes to increasing the strength of the steel sheet through solid solution strengthening. Moreover, it contributes to yield ratio reduction through formation of a hard second phase (for example, martensite). In order to obtain these effects, a content of 0.01% or more is required. On the other hand, if the content exceeds 0.50%, the generation of oxide scale containing firelite becomes remarkable, and the appearance of the steel sheet deteriorates. For this reason, Si was limited to the range of 0.01 to 0.50%. Note that the content is preferably 0.20 to 0.40%.
Mn: 1.4-2.2%
Mn dissolves to improve the hardenability of the steel and promote the formation of martensite. Further, it is an element that lowers the bainitic ferrite transformation start temperature and contributes to improvement of steel sheet toughness through refinement of the structure. In order to obtain these effects, a content of 1.4% or more is required. On the other hand, the content exceeding 2.2% lowers the toughness of the weld heat affected zone. For this reason, Mn was limited to the range of 1.4 to 2.2%. From the viewpoint of stable production of massive martensite, it is preferably 1.6 to 2.0%.
P: 0.025% or less P dissolves and contributes to an increase in steel sheet strength, but at the same time lowers toughness. For this reason, in this invention, it is preferable to reduce P as an impurity as much as possible. However, up to 0.025% is acceptable. Therefore, P is limited to 0.025% or less. In addition, Preferably it is 0.015% or less. Since excessive reduction raises the refining cost, it is preferable to make it about 0.001% or more.
S: 0.005% or less S forms coarse sulfide inclusions such as MnS in the steel and causes cracks such as slabs. Moreover, the ductility of a steel plate is reduced. Such a phenomenon becomes remarkable when the content exceeds 0.005%. For this reason, S was limited to 0.005% or less. In addition, Preferably it is 0.004% or less. In addition, although there is no problem even if S content is 0%, since excessive reduction raises refining cost, it is preferable to make it about 0.0001% or more.
Al: 0.005-0.10%
Al acts as a deoxidizer. Further, it is an element effective for fixing N that causes strain aging. In order to obtain these effects, a content of 0.005% or more is required. On the other hand, if the content exceeds 0.10%, the amount of oxide in the steel increases and the toughness of the base metal and the bath contact portion decreases. Further, when a steel material such as a slab or a steel plate is heated in a heating furnace, a nitride layer is easily formed on the surface layer, which may increase the yield ratio. For this reason, Al is limited to the range of 0.005 to 0.10%. In addition, Preferably it is 0.08% or less.
Nb: 0.02 to 0.10%
Nb is a solid solution in steel or precipitated as carbonitride, and suppresses the austenite grain size and suppresses the recrystallization of austenite grains. Is possible. It is also an element that precipitates finely as carbide or carbonitride and contributes to an increase in the strength of the steel sheet. During cooling after hot rolling, it precipitates as carbides or carbonitrides on the dislocations introduced by hot rolling, acts as the core of γ → α transformation, promotes intragranular formation of bainitic ferrite, This contributes to the formation of fine massive untransformed austenite and, in turn, fine massive martensite. In order to obtain these effects, a content of 0.02% or more is required. On the other hand, an excessive content exceeding 0.10% increases deformation resistance during hot rolling, which may make hot rolling difficult. An excessive content exceeding 0.10% leads to an increase in the yield strength of the main phase bainitic ferrite, making it difficult to ensure a yield ratio of 85% or less. For this reason, Nb was limited to the range of 0.02 to 0.10%. Note that the content is preferably 0.03 to 0.07%.
Ti: 0.001 to 0.030%
Ti fixes N as nitride and contributes to prevention of slab cracking. Moreover, it has the effect | action which precipitates finely as a carbide | carbonized_material and increases steel plate strength. In order to obtain such an effect, a content of 0.001% or more is required. On the other hand, if the content exceeds 0.030%, the bainitic ferrite transformation point is excessively raised and the toughness of the steel sheet is lowered. For this reason, Ti is limited to the range of 0.001 to 0.030%. Note that the content is preferably 0.005 to 0.025%.
Mo: 0.01-0.50%
Mo contributes to improving hardenability, attracts C in bainitic ferrite to untransformed austenite, and promotes martensite formation by improving the hardenability of untransformed austenite. Furthermore, it is an element that contributes to an increase in steel sheet strength by solid solution in steel and solid solution strengthening. In order to obtain these effects, a content of 0.01% or more is required. On the other hand, if the content exceeds 0.50%, martensite is formed more than necessary, and the toughness of the steel sheet is lowered. In addition, Mo is an expensive element, and a large amount thereof causes an increase in material cost. For this reason, Mo is limited to the range of 0.01 to 0.50%. Note that the content is preferably 0.10 to 0.40%.
Cr: 0.01-0.50%
Cr delays the γ → α transformation, contributes to improving hardenability, and has an action of promoting martensite formation. In order to acquire such an effect, 0.01% or more of content is required. On the other hand, if it exceeds 0.50%, defects tend to occur frequently in the weld. For this reason, Cr is limited to the range of 0.01 to 0.50%. Note that the content is preferably 0.20 to 0.45%.
Ni: 0.01-0.50%
Ni contributes to improving hardenability and promotes martensite formation. In addition, it is an element that further contributes to improved toughness. In order to obtain these effects, a content of 0.01% or more is required. On the other hand, if the content exceeds 0.50%, the effect is saturated and an effect commensurate with the content cannot be expected, which is economically disadvantageous. For this reason, Ni is limited to the range of 0.01 to 0.50%. Preferably, the content is 0.30 to 0.45%.
The above-described components are basic components. In the present invention, the above-described components are contained within the above-described content range, and the following formula (1)
Moeq (%) = Mo + 0.36Cr + 0.77Mn + 0.07Ni (1)
(Here, Mn, Ni, Cr, Mo: Content of each element (mass%))
It is preferable to adjust so that Moeq defined by the formula satisfies the range of 1.4 to 2.2%.
Moeq is an index representing the hardenability of untransformed austenite remaining in the steel sheet after passing through the cooling step. When Moeq is less than 1.4%, the hardenability of untransformed austenite is insufficient, and it transforms into pearlite or the like during the subsequent winding process. On the other hand, when Moeq exceeds 2.2%, martensite is generated more than necessary, and the toughness decreases. For this reason, Moeq is preferably limited to a range of 1.4 to 2.2%. If Moeq is 1.5% or more, the yield ratio is low and the deformability is further improved. For this reason, Moeq is more preferably 1.5% or more.
In the present invention, one or more selected from Cu: 0.50% or less, V: 0.10% or less, and B: 0.0005% or less as a selection element, as necessary, within the range of the components described above. And / or Ca: 0.0005 to 0.0050%.
One or more selected from Cu: 0.50% or less, V: 0.10% or less, B: 0.0005% or less
Cu, V, and B are all elements that contribute to increasing the strength of the steel sheet, and can be selected and contained as necessary.
V and Cu contribute to increasing the strength of the steel sheet through solid solution strengthening or precipitation strengthening. In addition, B segregates at the grain boundaries and contributes to increasing the strength of the steel sheet through improving hardenability. In order to obtain such effects, it is preferable to contain Cu: 0.01% or more, V: 0.01% or more, and B: 0.0001% or more. On the other hand, the content exceeding V: 0.10% reduces weldability. B: Content exceeding 0.0005% lowers the toughness of the steel sheet. Cu: Content exceeding 0.50% reduces hot workability. For this reason, when it contains, it is preferable to limit to Cu: 0.50% or less, V: 0.10% or less, B: 0.0005% or less.
Ca: 0.0005 to 0.0050%
Ca is an element that contributes to the control of the morphology of sulfides in which coarse sulfides are spherical sulfides, and can be contained as required. In order to acquire such an effect, it is preferable to contain Ca: 0.0005% or more. On the other hand, the content exceeding Ca: 0.0050% reduces the cleanliness of the steel sheet. For this reason, when it contains, it is preferable to limit to Ca: 0.0005 to 0.0050% of range.
The balance other than the components described above consists of Fe and inevitable impurities. As unavoidable impurities, N: 0.005% or less, O: 0.005% or less, Mg: 0.003% or less, Sn: 0.005% or less are acceptable.
Next, the reason for limiting the structure of the low yield ratio high strength hot rolled steel sheet of the present invention will be described.
The low yield ratio high strength hot-rolled steel sheet of the present invention has the above-described composition, and further includes a sheet thickness direction surface side layer (hereinafter sometimes simply referred to as a surface layer) and a sheet thickness direction inner surface side layer (hereinafter simply referred to as a surface layer). (Sometimes referred to as the inner layer). Thus, by having a different structure at each position in the plate thickness direction, it is possible to provide a low yield ratio and uniform deformability in the case of a steel pipe. The “sheet thickness direction surface side layer (surface layer)” herein refers to a region having a depth of less than 1.5 mm in the plate thickness direction from the front and back surfaces of the steel sheet. Further, the “thickness direction inner surface side layer (inner layer)” refers to a region having a depth of 1.5 mm or more in the thickness direction inward from the front and back surfaces of the steel plate.
The plate thickness direction surface side layer (surface layer) exhibits a tempered martensite phase single phase structure or a mixed structure of a tempered martensite phase and a tempered bainite phase. By setting it as such a structure | tissue, the hardness of the plate | board thickness direction surface side can be reduced and the outstanding uniform deformability can be comprised. Since pipe forming is bending deformation, the processing strain in the plate thickness direction increases as the distance from the plate thickness center increases, and becomes greater as the plate thickness increases. Therefore, it is important to adjust the surface layer structure.
When the hot-rolled steel sheet is subjected to non-uniform cooling history, for example, cooling that passes through the transition boiling region, the hardness increases locally, and hardness unevenness occurs. Such a problem can be avoided by making the surface layer a tempered martensite phase single phase structure or a mixed structure of a tempered martensite phase and a tempered bainite phase. In the case of a mixed structure, the mixing ratio of the tempered martensite phase and the tempered bainite phase is not particularly limited, but the tempered martensite phase is 60 to 100% in area ratio and the tempered bainite phase is changed. The area ratio is preferably 0 to 40% from the viewpoint of temper softening treatment. In addition, the above structure is 50% or more of the cumulative reduction rate in the temperature range of 930 ° C. or less in finish rolling, and the surface temperature is 100 ° C./s or more at the surface temperature in the cooling step after finish rolling. Primary cooling for cooling to a temperature equal to or lower than the martensite transformation start temperature (Ms point) at an average cooling rate, secondary cooling for retaining at a surface temperature of 600 ° C. or more for 1 s or more after completion of the primary cooling, After the completion of the secondary cooling, the tertiary cooling is performed at the temperature at the center of the plate thickness at an average cooling rate of 5 to 30 ° C / s to the cooling stop temperature in the temperature range of 600 to 450 ° C, and further cooling of the tertiary cooling. Cool from the stop temperature to the coiling temperature at the center of the plate thickness at an average cooling rate of 2 ° C / s or stay for 20s or more in the temperature range from the cooling stop temperature to the coiling temperature of the tertiary cooling. Can be obtained by sequentially performing the quaternary cooling. In addition, the tissue and the area ratio can be observed, measured, identified and calculated by the method described in Examples described later.
Furthermore, it is preferable that the hardness at a position of 0.5 mm in the thickness direction from the steel sheet surface is 95% or less of the maximum hardness in the thickness direction. That is, it is important from the viewpoint of ensuring the workability of the hot-rolled steel sheet and the pipe shape after pipe forming that the hardness at the position 0.5 mm from the steel sheet surface in the thickness direction does not become the maximum hardness in the thickness direction. is there. The maximum hardness in the plate thickness direction is preferably Vickers hardness HV0.5 and 165 points or more. Moreover, it is preferably 300 points or less, more preferably 280 points or less. The hardness is cooled to a temperature below the martensitic transformation start temperature (Ms point) at an average cooling rate of 100 ° C./s or higher at the surface temperature in the manufacturing conditions, particularly in the cooling step after finishing rolling. It can be obtained by performing primary cooling and secondary cooling that retains at a surface temperature of 600 ° C. or more for 1 s or more after completion of the primary cooling. Moreover, hardness can be measured by the method as described in the Example mentioned later.
On the other hand, the thickness direction inner surface side layer (inner layer) is composed of a main phase and a second phase in which a bulk martensite having an aspect ratio of less than 5.0 is dispersed as a second phase with a bainitic ferrite phase as a main phase. Presents an organization. Here, the main phase refers to a phase having an occupied area of 50% or more in area ratio. Bainitic ferrite is preferably 85% or more in area ratio, and more preferably 88.3% or more. The main phase bainitic ferrite is a phase having a substructure with a high dislocation density, and includes acicular ferrite and acicular ferrite. The bainitic ferrite does not include polygonal ferrite having a very low dislocation density or quasi (pseudo) polygonal ferrite with a substructure such as fine subgrains. In order to secure a desired high strength, it is necessary that fine carbonitride is precipitated in the bainitic ferrite as the main phase. The bainitic ferrite as the main phase has an average particle size of 10 μm or less. When the average particle size exceeds 10 μm, the work hardening ability in a low strain region of less than 5% is insufficient, and the yield strength decreases due to bending during spiral pipe making. By making the average particle size of the main phase fine, it is possible to ensure desired low-temperature toughness even when a large amount of martensite is contained.
The second phase in the inner layer is massive martensite with an area ratio of 1.4 to 15% and an aspect ratio of less than 5.0. The massive martensite referred to in the present invention is martensite generated from untransformed austenite in the old γ grain boundary or in the old γ grain in the cooling process after rolling. In the present invention, such massive martensite is dispersed between the old γ grain boundaries or the bainitic ferrite grains as the main phase and the bainitic ferrite grains. Martensite is harder than the main phase, and a large amount of movable dislocations can be introduced into the bainitic ferrite during processing, and the yield behavior can be a continuous yield type. Moreover, since martensite has a higher tensile strength than bainitic ferrite, a low yield ratio can be achieved. In addition, when the martensite is a massive martensite having an aspect ratio of less than 5.0, more movable dislocations can be introduced into the surrounding bainitic ferrite, which is effective in improving the deformability. If the aspect ratio of martensite is 5.0 or more, it becomes rod-shaped martensite (non-aggregated martensite) and the desired low yield ratio cannot be achieved, but if the rod-shaped martensite is less than 30% in terms of the area ratio with respect to the total amount of martensite. acceptable. The bulk martensite is preferably 70% or more in terms of the area ratio of the total amount of martensite. In addition, an aspect ratio can be measured by the method as described in the Example mentioned later.
In order to ensure such an effect, it is necessary to disperse massive martensite having an area ratio of 1.4% or more. If the bulk martensite is less than 1.4%, it becomes difficult to secure a desired low yield ratio. On the other hand, if the massive martensite exceeds 15% in area ratio, the low temperature toughness is remarkably lowered. For this reason, lump martensite was limited to the range of 1.4 to 15%. In addition, Preferably it is 10% or less. In addition, a 2nd phase may contain the bainite etc. of about 7.0% or less by area ratio other than a block martensite.
In addition, the above structure is 50% or more of the cumulative reduction rate in the temperature range of 930 ° C. or less in finish rolling, and the surface temperature is 100 ° C./s or more at the surface temperature in the cooling step after finish rolling. Primary cooling for cooling to a temperature equal to or lower than the martensite transformation start temperature (Ms point) at an average cooling rate, secondary cooling for retaining at a surface temperature of 600 ° C. or more for 1 s or more after completion of the primary cooling, After the completion of the secondary cooling, the tertiary cooling is performed at the temperature at the center of the plate thickness at an average cooling rate of 5 to 30 ° C / s to the cooling stop temperature in the temperature range of 600 to 450 ° C, and further cooling of the tertiary cooling. Cool from the stop temperature to the coiling temperature at the center of the plate thickness at an average cooling rate of 2 ° C / s or stay for 20s or more in the temperature range from the cooling stop temperature to the coiling temperature of the tertiary cooling. Can be obtained by sequentially performing the quaternary cooling.
The size of the massive martensite is preferably 5.0 μm or less at maximum and 0.5 to 3.0 μm on average. When the bulk martensite size exceeds 3.0 μm on average, it becomes a starting point of brittle fracture or facilitates the propagation of cracks, and the low temperature toughness decreases. On the other hand, if the average is less than 0.5 μm, the grains become too fine and the amount of movable dislocations introduced into the surrounding bainitic ferrite decreases. In addition, if it exceeds 5.0 μm at the maximum, the toughness decreases. Therefore, the size of the massive martensite is preferably 5.0 μm or less at maximum and 0.5 to 3.0 μm on average. In addition, the size was defined as “diameter” of 1/2 of the sum of the long side length and the short side length. The largest of them was regarded as the “maximum” of the size of the massive martensite, and the value obtained by arithmetically averaging the “diameter” of each obtained grain was designated as the “average” of the size of the massive martensite. The number of martensite to be measured is 100 or more.
In addition, the above structure is 50% or more of the cumulative reduction rate in the temperature range of 930 ° C. or less in finish rolling, and the surface temperature is 100 ° C./s or more at the surface temperature in the cooling step after finish rolling. Primary cooling for cooling to a temperature equal to or lower than the martensite transformation start temperature (Ms point) at an average cooling rate, secondary cooling for retaining at a surface temperature of 600 ° C. or more for 1 s or more after completion of the primary cooling, After the completion of the secondary cooling, the tertiary cooling is performed at the temperature at the center of the plate thickness at an average cooling rate of 5 to 30 ° C / s to the cooling stop temperature in the temperature range of 600 to 450 ° C, and further cooling of the tertiary cooling. Cool from the stop temperature to the coiling temperature at the center of the plate thickness at an average cooling rate of 2 ° C / s or stay for 20s or more in the temperature range from the cooling stop temperature to the coiling temperature of the tertiary cooling. Can be obtained by sequentially performing the quaternary cooling.
In addition, a structure | tissue, an area rate, and an average particle diameter can be observed and measured by the method as described in the Example mentioned later, can be identified and calculated.
Next, the preferable manufacturing method of the low yield ratio high-strength hot-rolled steel sheet of this invention is demonstrated.
In the present invention, the steel material having the above composition is subjected to a hot rolling process, a cooling process, and a winding process to obtain a hot rolled steel sheet.
In addition, it is not necessary to specifically limit the manufacturing method of the steel raw material to be used, and the molten steel having the above composition is melted by using a generally known melting method such as a converter or an electric furnace, and a normal casting method or the like is usually used. It is preferable to use a steel material such as a slab by a known melting method.
The obtained steel material is subjected to a hot rolling process.
In the hot rolling process, a steel material having the above composition is heated to a heating temperature of 1050 to 1300 ° C., subjected to rough rolling to form a sheet bar, and the sheet bar is subjected to a cumulative reduction in a temperature range of 930 ° C. or less. Rate: It is a process of applying hot rolling to 50% or more to obtain a hot-rolled steel sheet.
Heating temperature: 1050-1300 ° C
The steel material used in the present invention essentially contains Nb and Ti as described above. In order to secure a desired high strength by precipitation strengthening, it is necessary to dissolve these coarse carbides, nitrides and the like once and then finely precipitate them. Therefore, the heating temperature of the steel material is 1050 ° C. or higher. If it is less than 1050 degreeC, each element will remain undissolved and desired steel plate strength will not be obtained. On the other hand, when the temperature exceeds 1300 ° C., the crystal grains become coarse and the steel sheet toughness decreases. For this reason, the heating temperature of the steel material was limited to 1050-1300 ° C.
The steel material heated to the above heating temperature is subjected to rough rolling to form a sheet bar. The conditions for rough rolling need not be particularly limited as long as a sheet bar having a desired size and shape can be secured.
The obtained sheet bar is then finish-rolled to obtain a hot-rolled steel sheet having a desired size and shape. Finish rolling is a rolling with a cumulative reduction ratio of 50% or more in a temperature range of 930 ° C. or lower.
Cumulative rolling reduction in the temperature range below 930 ° C: 50% or more 50% cumulative rolling reduction in the temperature range below 930 ° C due to the refinement of bainitic ferrite and fine dispersion of massive martensite in the inner layer structure That's it. If the cumulative rolling reduction in the temperature range of 930 ° C or lower is less than 50%, the rolling amount is insufficient, and fine bainitic ferrite that is the main phase in the inner layer structure cannot be secured. In addition, dislocations that become precipitation sites such as NbC that promote nucleation of γ → α transformation are insufficient, intragranular formation of bainitic ferrite is insufficient, and massive untransformed γ to form massive martensite It cannot be dispersed finely and in large numbers. For this reason, the cumulative rolling reduction in the temperature range of 930 ° C. or lower in finish rolling is limited to 50% or more. The cumulative rolling reduction is preferably 80% or less. Even if the rolling reduction exceeds 80%, the effect is saturated, the occurrence of segregation becomes significant, and the Charpy impact test absorbed energy may be reduced.
The finish rolling temperature of finish rolling is preferably 850 to 760 ° C. from the viewpoints of steel plate toughness, steel plate strength, rolling load, and the like. When the finishing temperature of finish rolling exceeds 850 ° C and becomes high, it is necessary to increase the reduction amount per pass in order to increase the cumulative reduction rate in the temperature range of 930 ° C or less to 50% or more. There may be an increase in load. On the other hand, if the temperature is lower than 760 ° C., ferrite is produced during rolling, which causes coarsening of the structure and precipitates, and may reduce the low temperature toughness and strength.
The obtained hot-rolled steel sheet is then subjected to a cooling step.
The cooling step starts cooling immediately after finishing rolling, and performs primary cooling to cool to a temperature below the martensitic transformation start temperature (Ms point) at an average cooling rate of 100 ° C./s or more at the surface temperature, After cooling is completed, the secondary cooling is maintained for 1 s or more at a surface temperature of 600 ° C. or more, and after the completion of the secondary cooling, the temperature at the center of the plate thickness is 600 to 600 ° C. at an average cooling rate of 5 to 30 ° C./s. The tertiary cooling for cooling to the cooling stop temperature in the temperature range of ~ 450 ° C and the cooling stop temperature of the tertiary cooling to the winding temperature at an average cooling rate of 2 ° C / s or less at the plate thickness center temperature. It is a step of sequentially performing cooling or quaternary cooling that retains for 20 s or more in the temperature range from the cooling stop temperature of the tertiary cooling to the winding temperature, and the winding step is a winding temperature: 450 ° C. at the surface temperature. This is the winding process.
Immediately after finishing rolling, cooling is preferably started within 15 s.

In the primary cooling, cooling is performed until the surface temperature becomes an average cooling rate of 100 ° C./s or more and below the martensite transformation start temperature (Ms point). The cooling rate in the primary cooling means the average of the temperature range of 600 to 450 ° C. at the surface temperature. By this primary cooling, a martensite phase single phase structure or a mixed structure of martensite phase and bainite phase is formed on the steel sheet surface layer. The upper limit of the average cooling rate of primary cooling is not limited. Depending on the capacity of the cooling device used, it is possible to cool at a higher rate. In addition, what is necessary is just to set the time which retains below martensitic transformation start temperature (Ms point) with surface temperature according to a desired surface structure | tissue, However, It is less than 10 second, Preferably it is less than 7 second. If it stays for a long time in the temperature range below Ms point, the area | region used as the mixed structure of a martensite phase single phase or a martensite phase and a bainite phase will increase too much, and the plate | board thickness ratio which a desired structure | tissue will fall will decrease.

引 Secondary cooling is followed by primary cooling, but in secondary cooling, it is not particularly cooled, and is retained for 1 s or more at a surface temperature of 600 ° C. or higher by reheating or heating from the inside. By this secondary cooling, the martensite phase and the bainite phase are tempered, and the surface layer structure becomes a tempered martensite phase single phase structure or a mixed structure of the tempered martensite phase and the tempered bainite phase. When the steel sheet surface temperature is less than 600 ° C. and the residence time is less than 1 s, the tempering of the surface layer structure becomes insufficient. For this reason, secondary cooling was set as the process which makes 1 s or more stay at the temperature of a steel plate surface temperature of 600 degreeC or more. In addition, Preferably it is 2 s or more at the temperature of 600 degreeC or more. The upper limit of the residence time at a temperature of 600 ° C. or higher is not particularly limited. However, 6 s or less is preferable from the viewpoint of sufficiently securing the tertiary cooling condition in the central portion of the plate thickness and suppressing the formation of polygonal ferrite. The method for raising the surface temperature of the steel sheet to a temperature of 600 ° C. or higher includes a method using heat in the thickness direction and a method using an external heating facility, but is not particularly limited. A steel sheet surface layer structure is formed by primary cooling and secondary cooling, followed by tertiary cooling to form a steel sheet inner layer structure having bainitic ferrite as the main phase and massive martensite as the second phase.

The cooling rate of the tertiary cooling is an average cooling rate of 750 to 600 ° C., which is the polygonal ferrite formation temperature range, in the center of the plate thickness, and is in the range of 5 to 30 ° C./s. When the average cooling rate is less than 5 ° C./s, the structure of the inner layer becomes a structure mainly composed of polygonal ferrite, and it becomes difficult to secure a structure having a desired bainitic ferrite as a main phase. On the other hand, when the average cooling rate exceeds 30 ° C./s, the concentration of the alloy elements into untransformed austenite becomes insufficient, and the desired amount of massive martensite cannot be finely dispersed by the subsequent cooling. It is difficult to obtain a hot-rolled steel sheet having a low yield ratio and a desired excellent low-temperature toughness. Accordingly, the cooling rate at the central portion of the plate thickness is limited to 5 to 30 ° C./s, and preferably 5 to 25 ° C./s. The temperature at the center of the plate thickness can be obtained by heat transfer calculation or the like based on the surface temperature of the steel plate, the temperature of the cooling water, the amount of water, and the like.
The cooling stop temperature in the tertiary cooling is in the range of 600 to 450 ° C. If the cooling stop temperature is higher than the above-described temperature range, it is difficult to secure a structure of the inner layer whose main phase is desired bainitic ferrite. On the other hand, when the cooling stop temperature is lower than the above temperature range, the untransformed γ is almost completely transformed and a desired amount of massive martensite cannot be secured.
In the present invention, quaternary cooling is performed following the primary to tertiary cooling described above. FIG. 1 schematically shows the cooling in the temperature range from the cooling stop temperature of the tertiary cooling to the winding temperature as the fourth cooling at the plate thickness center temperature. The fourth cooling is slow cooling as shown in FIG. By slowly cooling this temperature range, alloy elements such as C are further diffused into the untransformed γ, the untransformed γ is stabilized, and the subsequent cooling facilitates the formation of massive martensite. As such slow cooling, is cooling from the cooling stop temperature of the above-mentioned tertiary cooling to the coiling temperature at the sheet thickness center temperature, an average cooling rate of 2 ° C / s or less, preferably 1.5 ° C / s or less? Alternatively, the cooling is to be retained for 20 seconds or more in the temperature range from the cooling stop temperature of the above-described tertiary cooling to the coiling temperature. When cooling from the cooling stop temperature of the secondary cooling to the coiling temperature at an average cooling rate exceeding 2 ° C./s, alloy elements such as C cannot sufficiently diffuse into the untransformed γ, and the stability of the untransformed γ As in the cooling shown by the dotted line in FIG. 1, the untransformed γ remains between the bainitic ferrites, resulting in a rod-like shape, making it difficult to produce the desired massive martensite.
In addition, it is preferable to perform this quaternary cooling by stopping water injection at the latter stage of the run-out table. In the case of a steel plate having a thin plate thickness, it is preferable to adjust by completely removing the cooling water remaining on the steel plate, installing a heat insulating cover, or the like in order to ensure desired cooling conditions. Furthermore, in order to ensure a residence time of 20 seconds or more in the above temperature range, it is preferable to adjust the conveyance speed.
After the fourth cooling, the hot rolled steel sheet is subjected to a winding process.
The winding process is a winding process at a surface temperature and a winding temperature of 450 ° C. or higher.
If the coiling temperature is less than 450 ° C., the desired low yield ratio cannot be realized. For this reason, the coiling temperature was limited to 450 ° C. or higher. By setting it as the above-mentioned process, it can be made to retain for a predetermined time or more in the temperature range in which ferrite and austenite coexist.
A hot-rolled steel sheet manufactured by the above-described manufacturing method is used as a pipe-forming material, and is subjected to a normal pipe-making process to be a spiral steel pipe or an electric-welded steel pipe. The pipe making process is not particularly limited, and any ordinary process can be applied.
Hereinafter, the present invention will be described in more detail based on examples.

The molten steel having the composition shown in Table 1 was made into a slab (thickness: 220 mm) by a continuous casting method to obtain a steel material. Next, these steel materials are heated to the heating temperature shown in Table 2 and subjected to rough rolling to form a sheet bar, and then the sheet bar is subjected to finish rolling under the conditions shown in Table 2 to obtain a hot-rolled steel sheet (sheet thickness: A hot rolling process of 8 to 25 mm) was performed. Immediately after finishing rolling, the obtained hot-rolled steel sheet was subjected to a cooling process including primary cooling to quaternary cooling shown in Table 2. After the cooling step, a winding step of winding at a winding temperature shown in Table 2 and then allowing to cool was performed.
From the obtained hot-rolled steel sheet, a test piece was collected and subjected to a structure observation, a tensile test, an impact test, and a hardness test.
The test method is as follows.
(1) Microstructure observation From the obtained hot-rolled steel sheet, a microstructural specimen was taken so that the cross section in the rolling direction (L cross section) became the observation surface. The test piece was polished and subjected to Nital corrosion, and the structure was observed and imaged using an optical microscope (magnification: 500 times) or an electron microscope (magnification: 2000 times). The type of tissue, the tissue fraction (area ratio) of each phase, and the average particle diameter were measured from the obtained inner layer structure photograph using an image analyzer. In addition, about the surface layer, only the identification of the kind of structure | tissue was performed from the structure | tissue photograph.
The average particle size of bainitic ferrite, which is the main phase in the inner layer structure, was determined by a cutting method in accordance with JISG 0552. The aspect ratio of the martensite grain is the ratio of the length in the longitudinal direction of each grain, that is, the direction in which the grain size is maximum (long side) and the length in the direction perpendicular to the length (short side), (long side). / (Short side). Martensite grains having an aspect ratio of less than 5.0 are defined as massive martensite. Martensite having an aspect ratio of 5.0 or more is referred to as “bar-shaped” martensite. In addition, the size of the massive martensite is 1/2 the sum of the long side length and the short side length of each grain of the massive martensite, and the diameter of each obtained grain is arithmetically averaged. The average size of martensite was used. In addition, the largest value among the diameter of each grain of massive martensite was made into the maximum of the magnitude | size of massive martensite. The measured martensite grains were 100 or more.
(2) Tensile test From the obtained hot-rolled steel sheet, the tensile test piece (API-5L is specified) so that the tensile direction is perpendicular to the rolling direction (sheet width direction) and 30 degrees from the rolling direction. Full thickness test pieces (width 38.1 mm; GL 50 mm) were collected and subjected to a tensile test in accordance with ASTM A 370 regulations to determine tensile properties (yield strength YS, tensile strength TS).
(3) Impact test V-notch test specimens were taken from the obtained hot-rolled steel sheet so that the longitudinal direction of the test specimen was perpendicular to the rolling direction, and the Charby impact test was conducted in accordance with ASTM 370 regulations. The fracture surface transition temperature vTrs (° C.) was obtained.
(4) Hardness test From the obtained hot-rolled steel sheet, a specimen for hardness measurement was collected, and the cross-sectional hardness was measured using a Vickers hardness tester (test force: 4.9 N) (load: 500 g). Measurements were continuously made from the surface of the steel sheet in the thickness direction at intervals of 0.5 mm, and the hardness at the 0.5 mm position in the thickness direction (depth direction) from the surface and the maximum hardness in the thickness direction were determined. And the hardness distribution is good when the maximum hardness in the thickness direction is 300 points or less and the ratio of the hardness at the depth of 0.5 mm from the surface to the maximum hardness in the thickness direction is 95% or less. evaluated.
Next, a spiral steel pipe (outer diameter: 1067 mmφ) was manufactured by a spiral pipe making process using the obtained hot-rolled steel sheet as a pipe material. From the obtained steel pipe, take a tensile test piece (test piece specified in API) so that the tensile direction is the pipe circumferential direction, conduct a tensile test in accordance with the provisions of ASTMA 370, and obtain tensile properties (yield). Strength YS and tensile strength TS) were measured. From the obtained results, ΔYS (= steel pipe YS−steel sheet 30 ° YS) was calculated, and the degree of strength reduction due to pipe making was evaluated.
The obtained results are shown in Table 3.

None of the inventive examples were subjected to a special heat treatment, the yield strength in the direction of 30 degrees from the rolling direction was 480 MPa or more, the tensile strength in the sheet width direction was 600 MPa or more, and the fracture surface transition temperature vTrs was − It has excellent toughness of 80 ° C or less and a low yield ratio high strength high toughness hot rolled steel sheet with a yield ratio of 85% or less. On the other hand, in the comparative example that is out of the scope of the present invention, a hot-rolled steel sheet having the desired characteristics has not been obtained depending on whether the toughness is reduced or the low yield ratio is not ensured.

In addition, in all of the examples of the present invention, after the pipes are formed into steel pipes, there is little decrease in strength due to the pipe making, and the steel sheet is suitable as a material for spiral steel pipes or ERW steel pipes.

Claims

In mass%, C: 0.03-0.10%, Si: 0.01-0.50%, Mn: 1.4-2.2%, P: 0.025% or less, S: 0.005% or less, Al: 0.005-0.10%, Nb: 0.02-0.10% Ti: 0.001 to 0.030%, Mo: 0.01 to 0.50%, Cr: 0.01 to 0.50%, Ni: 0.01 to 0.50%, and the composition consisting of the balance Fe and inevitable impurities,
The inner layer is composed of bainitic ferrite having an average particle size of 10 μm or less as a main phase, and the second phase is a structure containing massive martensite with an area ratio of 1.4 to 15% in area ratio: less than 5.0,
The surface layer is a structure composed of a tempered martensite phase or a tempered martensite phase and a tempered bainite phase.
A hot-rolled steel sheet characterized by that.
2. The hot-rolled steel sheet according to claim 1, wherein the composition is a composition satisfying a mass% and Moeq defined by the following formula (1) in a range of 1.4 to 2.2%.
Record
Moeq (%) = Mo + 0.36Cr + 0.77Mn + 0.07Ni (1)
Here, Mn, Ni, Cr, Mo: Content of each element (mass%)
In addition to the composition, the composition further contains one or more selected from Cu: 0.50% or less, V: 0.10% or less, and B: 0.0005% or less in terms of mass%. The hot rolled steel sheet according to 1 or 2.
The hot rolled steel sheet according to any one of claims 1 to 3, further comprising Ca: 0.0005 to 0.0050% by mass% in addition to the composition.
The hot rolled steel sheet according to any one of claims 1 to 4, wherein the bulk martensite has a maximum size of 5.0 µm or less and an average of 0.5 to 3.0 µm.
The hot-rolled steel sheet according to any one of claims 1 to 5, wherein the hardness at a depth of 0.5 mm from the surface in the thickness direction is 95% or less of the maximum hardness in the thickness direction.
The steel material is subjected to a hot rolling process, a cooling process, and a winding process to make a hot rolled steel sheet.
The steel material in mass%,
C: 0.03-0.10%, Si: 0.01-0.50%, Mn: 1.4-2.2%, P: 0.025% or less, S: 0.005% or less, Al: 0.005-0.10%, Nb: 0.02-0.10%, Ti: 0.001 Steel material having a composition comprising the balance Fe and inevitable impurities, including 0.030%, Mo: 0.01-0.50%, Cr: 0.01-0.50%, Ni: 0.01-0.50%,
In the hot rolling step, the steel material is heated to a heating temperature of 1050 to 1300 ° C., the heated steel material is subjected to rough rolling to form a sheet bar, and the sheet bar is heated at a temperature range of 930 ° C. or less. Cumulative rolling reduction: It is a process to make a hot-rolled steel sheet by applying finish rolling to 50% or more,
The cooling step is started immediately after finishing rolling, and at the surface temperature, cooling at an average cooling rate of 100 ° C./s or higher to a temperature below the martensite transformation start temperature, and after the completion of the primary cooling Secondary cooling for 1 s or more at a surface temperature of 600 ° C or higher, and after completion of the secondary cooling, 600 to 450 ° C at an average cooling rate of 5 to 30 ° C / s at the center temperature of the plate thickness Cooling to the cooling stop temperature in the temperature range, and further cooling from the cooling stop temperature of the tertiary cooling to the coiling temperature at the center temperature of the plate thickness at an average cooling rate of 2 ° C / s or less? Or a step of sequentially performing quaternary cooling for retaining for 20 s or more in the temperature range from the cooling stop temperature to the coiling temperature of the tertiary cooling,
The winding step is a step of winding at a winding temperature of 450 ° C. or more at the surface temperature,
A method for producing a hot-rolled steel sheet.
The method for producing a hot-rolled steel sheet according to claim 7, wherein the composition is a composition satisfying a mass% and Moeq defined by the following formula (1) in a range of 1.4 to 2.2%.
Record
Moeq (%) = Mo + 0.36Cr + 0.77Mn + 0.07Ni (1)
Here, Mn, Ni, Cr, Mo: Content of each element (mass%)
In addition to the composition, the composition further contains one or more selected from Cu: 0.50% or less, V: 0.10% or less, and B: 0.0005% or less in terms of mass%. A method for producing a hot-rolled steel sheet according to 7 or 8.
10. The method for producing a hot-rolled steel sheet according to claim 7, further comprising Ca: 0.0005 to 0.0050% by mass% in addition to the composition.