Steel sheet pile and method for manufacturing the same

Abstract

In a steel sheet pile according to the present invention, a carbon equivalent CE.sub.N is 0.260 to 0.500, a structure includes a ferrite, a pearlite, a Widmansttten ferrite, and a precipitate, the precipitate is one or both of Nb carbonitride and V carbonitride, a total number density of the precipitate is 0.10 to 0.30 pieces/m.sup.2, a total area ratio of the ferrite and the pearlite is 70% or more, an area ratio of the Widmansttten ferrite is 1% or more, an average grain size of the ferrite and the pearlite is 10 to 80 m, and a yield strength is 460 MPa or more.

Claims

1. A steel sheet pile, wherein a chemical composition consists of, in terms of mass %: C: 0.05 to 0.18%; Si: 0.10 to 0.50%; Mn: 0.50 to 1.50%; Nb: 0.040 to 0.050%; V: 0.20 to 0.30%; Cu: 0 to 0.40%; Ni: 0 to 1.00%; Mo: 0 to 1.00%; Cr: 0 to 1.00%; Al: limited to less than 0.05%; P: 0.040% or less; S: 0.040% or less; and remainder including Fe and impurities, a carbon equivalent calculated by Expression 1 and Expression 2 is 0.260 to 0.500, a structure includes a ferrite, a pearlite, a Widmansttten ferrite, and a precipitate, the precipitate is one or both of Nb carbonitride and V carbonitride, a number density of the precipitate is 0.10 to 0.30 pieces/m.sup.2, a total area ratio of the ferrite and the pearlite is 70% or more, an area ratio of the Widmansttten ferrite is 1% or more, an average grain size of the ferrite and the pearlite is 10 to 80 m, a yield strength is 460 to 550 MPa and a tensile strength is 550 to 740 MPa,
CE.sub.N=<C>+f(C){<Mn>/6+<Si>/24+<Ni>/20+(<Cr>+<Mo>+<Nb>+<V>)/5}:Expression 1,
f(C)=0.75+0.25tan h{20(<C>0.12)}:Expression 2, and <C>, <Mn>, <Si>, <Ni>, <Cr>, <Mo>, <Nb>, and <V> express amounts of each element in terms of mass %, in which an amount of an element which is not included is considered to be 0%.

2. A method for manufacturing the steel sheet pile according to claim 1, the method comprising: heating a steel slab consisting of the chemical composition according to claim 1 to 1100 to 1350 C.; hot-rolling the steel slab under a condition in which a cumulative reduction at a region of 900 C. or more is 90% or more and a finishing temperature is 850 C. or more to obtain the steel sheet pile; and cooling the steel sheet pile.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) FIG. 1 is a graph indicating a relationship between strength and an average grain size of ferrite and pearlite, and a relationship between elongation and the average grain size of the ferrite and the pearlite according to the present embodiment.

(2) FIG. 2 is a flow chart indicating a method for manufacturing a steel sheet pile according to the present embodiment.

EMBODIMENTS OF THE INVENTION

(3) Hereinafter, a steel sheet pile according to an embodiment of the present invention will be described in detail. In the present embodiment, strength represents both of tensile strength and yield strength. In the present embodiment, a weld portion of the steel sheet pile represents a weld metal and a heat affected zone of the welded steel sheet pile. In the present embodiment, a base metal of the steel sheet pile represents a part other than the weld portion in the welded steel sheet pile (i.e. the base metal of the steel sheet pile is substantially equal to steel sheet pile before welding).

(4) In order to secure strength and toughness of the base metal of the steel sheet pile and toughness of the weld portion of the steel sheet pile, it is very important to control hardenability of the steel sheet pile. Controlling the hardenability is an optimization of an amount of C and an amount of other alloy components improving hardenability. The hardenability is evaluated by a carbon equivalent. An expression for calculating the carbon equivalent from amounts of each of the alloy components has been proposed.

(5) In a case in which the hardenability is limited in order to secure toughness of the weld portion of the steel sheet pile, strength of the base metal decreases. In this case, it is typical that the strength of the base metal is increased by performing hot-rolling at a low temperature in manufacturing stage. On the other hand, it is preferable to perform the hot-rolling on the steel sheet pile at a high temperature in view of improving productivity and decreasing load on a mill roll. Therefore, it is difficult to satisfy all of enhancing strength and toughness of the base metal of the steel sheet pile, enhancing toughness of the weld portion of the steel sheet pile, and productivity. The inventors made a study of securing strength of the base metal and the weld portion of the steel sheet pile with a precipitation strengthening. Typically, the precipitation strengthening deteriorates toughness. However, the inventors conducted a study and found that, when appropriate amounts of Nb and V are included and a cumulative reduction within a high temperature range of 900 C. or more is 90% or more in the hot-rolling, precipitation of Nb carbonitride and V carbonitride is accelerated and a Widmansttten structure is formed, and thus, coarsening of ferrite and pearlite is suppressed. The toughness of the steel sheet pile can be enhanced by suppressing coarsening of the ferrite and the pearlite.

(6) The inventers further made a study to seek an optimization of a reduction and a temperature in the hot-rolling and an optimization of amounts of Nb and V and hardenability, and thus, achieved to obtain high strength steel sheet pile having yield stress of 460 MPa or more without deteriorating toughness of the base metal and the weld portion by controlling precipitation of the Nb carbonitride and the V carbonitride.

(7) In the present invention, a hardenability index is a carbon equivalent CE.sub.N calculated by the known expression 1 and expression 2.
CE.sub.N=<C>+f(C){<Mn>/6+<Si>/24+<Ni>/20+(<Cr>+<Mo>+<Nb>+<V>)/5}(Expression 1)
f(C)=0.75+0.25tan h{20(<C>0.12)}(Expression 2)

(8) <C>, <Mn>, <Si>, <Ni>, <Cr>, <Mo>, <Nb>, and <V> express amounts of each element in terms of mass %, in which an amount of an element which is not included is considered as 0%.

(9) First, a chemical composition of the steel sheet pile according to the present embodiment is described. The unit % regarding the chemical composition represents mass %.

(10) (C: 0.05 to 0.18%)

(11) C is an element which is effective for enhancing strength of steel. The lower limit of an amount of C of the steel sheet pile according to the present embodiment is 0.05% to secure strength. On the other hand, when C is excessively included, the toughnesses of the base metal and the heat affected zone of the steel sheet pile decrease. Therefore, in the present embodiment, an upper limit of the amount of C is 0.18%. The lower limit of the amount of C is preferably 0.10% to further optimize a balance of the strength and the toughness.

(12) (Si: 0.10 to 0.50%)

(13) Si is a deoxidizing element. The lower limit of an amount of Si is 0.10% to sufficiently deoxidize. In addition, Si is an element having an effect of improving the strength and it is preferable that the amount of Si is 0.20% or more to obtain the effect. On the other hand, when the amount of Si is excess, the toughnesses of the base metal and the heat affected zone of the steel sheet pile decrease, and thus, the upper limit of the amount of Si is 0.50%.

(14) (Mn: 0.50 to 1.50%)

(15) Mn enhances the hardenability of the steel, and is effective for refining structure and for securing the strength and the toughness. In the present embodiment, the lower limit of an amount of Mn is 0.50% to secure the strength of the base metal of the steel sheet pile. On the other hand, when the amount of Mn is excess, the toughness of the weld portion of the steel sheet pile decreases due to increasing of the hardenability. Therefore, in the present embodiment, an upper limit of the amount of Mn is 1.50%. The upper limit of the amount of Mn is preferably 1.30% to further optimize a ratio of the strength and the toughness.

(16) (Nb: 0.040 to 0.050%)

(17) Nb is a very important element in the present embodiment. Nb combines with C and/or N to form a Nb carbonitride. The Nb carbonitride improves the strength of the base metal and the weld portion of the steel sheet pile by precipitation strengthening. The amount of Nb is 0.040% or more to obtain the effect. On the other hand, when more than 0.050% of Nb is included, the Nb carbonitride deteriorates the toughness of the base metal of the steel sheet pile, and increasing of the hardenability deteriorates the toughness of the weld portion of the steel sheet pile. Therefore, an upper limit of the amount of Nb is 0.050%. As noted above, the amount of Nb is 0.040 to 0.050%. The amount of Nb is preferably 0.040 to 0.045%.

(18) (V: 0.20 to 0.30%)

(19) V is a very important element in the present embodiment. V combines with C and/or N to form a V carbonitride. The V carbonitride improves the strength of the base metal and the weld portion of the steel sheet pile by precipitation strengthening. The amount of V is 0.20% or more to obtain the effect. On the other hand, when more than 0.30% of V is included, the toughness of the base metal of the steel sheet pile is deteriorated, and increasing of the hardenability deteriorates the toughness of the weld portion of the steel sheet pile. Therefore, an upper limit of the amount of V is 0.30%. As noted above, the amount of V is 0.20 to 0.30%. The amount of V is preferably 0.20 to 0.23%.

(20) (Al: Less than 0.05%)

(21) Al is a deoxidizing element, however, if Si which is other deoxidizing element is included, Al is not necessary essential. Therefore, the lower limit of an amount of Al is not limited. On the other hand, when the amount of Al is excess, the toughness of the steel sheet pile decreases due to formation of coarse Al oxide. Therefore, the amount of Al is limited to less than 0.05%. An upper limit of the amount of Al is preferably 0.03%, and more preferably 0.02%.

(22) (Remainder: Fe and Impurities)

(23) A remainder of the chemical composition of the steel sheet pile according to the present embodiment is Fe and impurities. The impurities represent a composition which is mixed through a material such as ore or scrap or through several factors of manufacturing process of the steel material and which is acceptable as long as a property of the steel sheet pile according to the present embodiment is not deteriorated thereby. In the present embodiment, typical impurities include P and S. P is a harmful composition which may embrittle the steel sheet pile and may deteriorate the strength of the base metal and the weld portion of the steel sheet pile. P may be included as long as an amount of P is 0.040% or less; however, the smaller the amount of P is, the more preferable it is. In addition, S is a harmful composition which may deteriorate the strength and the toughness of the base metal and the weld portion of the steel sheet pile. S may be included as long as the amount of S is 0.040% or less; however, the smaller the amount of S, the more preferable it is.

(24) Moreover, in the present embodiment, optionally, one or more of Cu, Ni, Mo, and Cr may be included as optional elements. Including such elements is not essential, and thus, the lower limits of the amounts of the elements are 0%.

(25) (Cu: 0 to 0.40%)

(26) Cu is an element enhancing the strength of the base metal and the weld portion of the steel sheet pile by solid-solution into structure of the steel sheet pile. In order to obtain the effect, it is preferable that the amount of Cu is 0.05% or more. On the other hand, when Cu is excessively included, precipitation of CuS and deterioration of surface property may be caused, and thus, it is preferable that an upper limit of the amount of Cu is 0.40%.

(27) (Ni: 0 to 1.00%)

(28) Ni is an element enhancing the hardenability of the steel sheet pile and enhancing the strength and the toughness of the base metal and the weld portion of the steel sheet pile by solid-solution into the structure of the steel sheet pile. In order to obtain the effect, it is preferable that the amount of Ni is 0.10% or more. On the other hand, Ni is costly, and thus, it is preferable that the upper limit of the amount of Ni is 1.00%. The upper limit of the amount of Ni is more preferably 0.50%, and much more preferably 0.30%. When Cu is included, it is preferable that both of Cu and Ni are included in order to prevent the surface property from deteriorate.

(29) (Mo: 0 to 1.00%)

(30) Mo is an element enhancing the strength of the base metal and the weld portion of the steel sheet pile even if an amount thereof is extremely small. In order to obtain the effect, it is preferable that the amount of Mo is 0.10% or more. On the other hand, Mo enhances the strength of a steel in a high temperature (i.e. the steel sheet pile before rolling), and when Mo is excessively included, a deformation resistance of the steel sheet pile before rolling may increase which causes the mill roll to crack in rolling. Therefore, it is preferable that an upper limit of the amount of Mo is 1.00%. The upper limit of the amount of Mo is more preferably 0.50%. In addition, the lower limit of the amount of Mo is preferably 0.30%.

(31) (Cr: 0 to 1.00%)

(32) Cr is an element enhancing the hardenability of the steel sheet pile and being effective to increase the strength. In order to obtain the effects, it is preferable that the amount of Cu is 0.10% or more. On the other hand, when Cr is excessively included, the toughness of the weld portion and the base metal of the steel sheet pile may be deteriorated. Therefore, it is preferable that an upper limit of the amount of Cr is 1.00%. The upper limit of the amount of Cr is more preferably 0.50% and much more preferably 0.30%.

(33) (Carbon Equivalent CE.sub.N: 0.260 to 0.500)

(34) In the steel sheet pile according to the present embodiment, in order to secure the strength of the base metal and the weld portion of the base metal without deteriorating the toughness of the weld portion, a carbon equivalent CE.sub.N calculated by the known expression 1 and expression 2 is 0.260 to 0.500. The carbon equivalent CE.sub.N is an index of the hardenability. In order to secure yield stress of 460 MPa or more, it is necessary that a lower limit of the carbon equivalent CE.sub.N is 0.260. On the other hand, in order to secure the toughness of the base metal and the weld portion of the steel sheet pile, it is necessary that an upper limit of the carbon equivalent CE.sub.N is 0.500.
CE.sub.N=<C>+f(C){<Mn>/6+<Si>/24+<Ni>/20+(<Cr>+<Mo>+<Nb>+<V>)/5}(Expression 1)
f(C)=0.75+0.25tan h{20(<C>0.12)}(Expression 2)

(35) <C>, <Mn>, <Si>, <Ni>, <Cr>, <Mo>, <Nb>, and <V> express amounts of each element in terms of mass %.

(36) Next, the structure of the steel sheet pile according to the present embodiment will be described. A portion in which the structure of the steel sheet pile is defined is not limited; however, for example, when the structure of a web width portion in the steel sheet pile (position spaced in a width direction of the web from the end of the web by a length of of the width of the web) is controlled as described below, it can be considered that substantially all over the structure of the steel sheet pile is controlled adequately.

(37) (Structure: Including a Ferrite, a Pearlite, a Widmansttten Ferrite, and a Precipitate)

(38) (Precipitate: One or Two of Nb Carbonitride and V Carbonitride)

(39) The structure of the steel sheet pile according to the present embodiment includes a ferrite, a pearlite, and a Widmansttten ferrite. In addition, it is preferable that the structure of the steel sheet pile according to the present embodiment include a precipitate. The precipitate is a carbonitride such as V(C, N), Nb(C, N), etc. A precipitation strengthening due to fine precipitate and a miniaturization of the structure due to a pinning effect of the fine precipitate secure the toughness of the base metal and the weld portion of the steel sheet pile and increase the strength of the base metal and the weld portion of the steel sheet pile. V(C, N) is called as V carbonitride and Nb(C, N) is called as Nb carbonitride.

(40) The pearlite described herein is a layered structure of cementite and ferrite as well-known in general. The ferrite described herein is a normal ferrite having granular shape.

(41) The Widmansttten ferrite is a structure which grows with rate-controlled by diffusion of carbon atoms, in which Fe atoms transforms and grows with shear transformation as like to martensite transformation, and which is a tabular ferrite structure. The Widmansttten ferrite is distinguished from the above-described normal ferrite.

(42) The ferrite included in the pearlite and an acicular ferrite also have the tabular shape; however, the Widmansttten ferrite is distinguished from the ferrite included in the pearlite and the acicular ferrite in the following points. The ferrite included in the pearlite constructs the layered structure together with the cementite as described above. On the other hand, the Widmansttten ferrite constructs the layered structure without the cementite. The acicular ferrite radially grows with centering upon nonmetallic inclusion and the like. On the other hand, the Widmansttten ferrite grows in tabular form from a boundary of an austenite or from a ferrite which has already transformed.

(43) In the present embodiment, the Widmansttten ferrite is defined as a tabular ferrite in which an aspect ratio L/W of a length L to a width W is 4 or more, which is not accompanied by a layered cementite, and which grows from a boundary of an austenite or from a ferrite which has already transformed. When the structure of two-dimensional cross section of the steel sheet pile is observed, the Widmansttten ferrite can be distinguished from the normal ferrite, the ferrite included in the pearlite, and the acicular ferrite by the definition.

(44) Including the ferrite increases the toughness. Including the pearlite increases the strength. An effect of preventing the ferrite and the pearlite from coarsening can be obtained by including the Widmansttten ferrite. Increasing of the toughness of the steel sheet pile can be achieved by preventing the ferrite and the pearlite from coarsening.

(45) (A Total Area Ratio of Ferrite and Pearlite: 70% or More)

(46) (An Area Ratio of Widmansttten Ferrite: 1% or More)

(47) A total area ratio of the ferrite and the pearlite of the steel sheet pile according to the present embodiment is 70% or more. Thereby, the strength and the toughness of the base metal and the weld portion of the steel sheet pile can be sufficiently increased. A structure other than the ferrite, the pearlite, and the Widmansttten ferrite, for example, bainite and the like may form as remainder structure. Including such a remainder structure is acceptable as long as the total area ratio of the ferrite and the pearlite are kept. It is not necessary to limit a content ratio of the ferrite, the pearlite, and the Widmansttten ferrite. On the other hand, an amount of the Widmansttten ferrite is 1% or more in terms of area %. When the area ratio of Widmansttten ferrite is less than 1%, the above-described effect exhibited by the Widmansttten ferrite cannot be obtained.

(48) The total area ratio of the ferrite and the pearlite, and the area ratio of Widmansttten ferrite were measured in accordance with a method of International Institute of Welding. That is, a grid having a total of 100 pieces of crossover points, i.e. 10 vertical pieces by 10 horizontal pieces of crossover point was mounted on a optical microscope photograph of structure, and structures regarding each crossover points were point-counted. The amounts of each of the structures were quantified by repeating the above-described method and averaging.

(49) (A Total Number Density of Precipitate: 0.10 to 0.30 Pieces/m.sup.2)

(50) When a total number per unit area of precipitate which is one or two of the Nb carbonitride and the V carbonitride is less than 0.10 pieces/m.sup.2, sufficiently strength cannot be obtained. On the other hand, when the total number per unit area of the Nb carbonitride and the V carbonitride is more than 0.30 pieces/m.sup.2, the toughness of the steel sheet pile deteriorates. Therefore, the total number density of the Nb carbonitride and the V carbonitride is 0.10 to 0.30 pieces/m.sup.2. The preferable total number per unit area of the Nb carbonitride and the V carbonitride is 0.11 to 0.25 pieces/m.sup.2. The total number per unit area of the Nb carbonitride and the V carbonitride can be measured by analyzing a sample, which is an extraction replica, with a transmission electron microscope.

(51) It is not necessary to define the size of the Nb carbonitride and the V carbonitride. On the other hand, it is assumed that a Nb carbonitride and a V carbonitride whose major axis is less than 10 nm do not substantially affect the properties of the steel sheet pile, and the Nb carbonitride and the V carbonitride whose major axis is less than 10 nm cannot be observed with the above-described extraction replica method. Therefore, the lower limit of the major axis of the Nb carbonitride and the V carbonitride is substantially 10 nm. In addition, when the Nb carbonitride and the V carbonitride having the above-described number density are included, a Nb carbonitride and a V carbonitride having a major axis of more than 300 nm are not formed. The inventors observed structures of various steel sheet piles according to the present embodiment, and as a result, the inventors did not find Nb carbonitride and V carbonitride having a major axis of more than 300 nm. Therefore, an upper limit of the major axis of the Nb carbonitride and the V carbonitride is substantially 300 nm.

(52) (Average Grain Size of Ferrite and Pearlite: 10 to 80 m)

(53) When an average grain size of the ferrite and the pearlite (hereinafter, abbreviated as average grain size or grain size as appropriate) is more than 80 m, the toughness and the strength of the base metal and the weld portion of the steel sheet pile may be deteriorated. On the other hand, when the average grain size of the steel sheet pile is less than 10 m, an elongation of the steel sheet pile may be extremely deteriorated. If the elongation is deteriorated, the toughness is deteriorated. Therefore, it is preferable that the average grain size of the steel sheet pile is 10 to 80 m.

(54) The average grain size of the structure of the steel sheet pile according to the present embodiment can be obtained by observing with an optical microscope in accordance with JIS G 0551. The grain size of the pearlite structure can be obtained by applying the above-described method for measuring the grain size of ferrite grain to a pearlite colony (island of pearlite described in JIS G 0551). The average grain size of ferrite and pearlite represents the average grain size of both the ferrite and the pearlite. If, along the average grain size of either the ferrite or the pearlite is less than 10 m or more than 80 m, the average grain size of both of the ferrite and the pearlite is 10 to 80 m, it is determined that the above-described definition is satisfied.

(55) When the average grain size of the structure described above is measured, the Widmansttten ferrite is ignored. In addition, an major axis of the Widmansttten ferrite is typically 5 to 30 m, and a variation of the major axis within the range does not affect the property of the steel sheet pile according to the present embodiment. Therefore, it is not necessary to define a size of the Widmansttten ferrite in the present embodiment.

(56) FIG. 1 represents a relationship between the average grain size (m) of the ferrite and the pearlite of the steel sheet pile and the strength <YP (MPa)> and a relationship between the average grain size (m) of the ferrite and the pearlite of the steel sheet pile and the elongation (%) in accordance with test results using a portion of samples. When the average grain size of the ferrite and the pearlite of the steel sheet pile is more than 80 m, the yield strength may be less than 460 MPa, and when the average grain size of the ferrite and the pearlite of the steel sheet pile is less than 10 m, the elongation may be deteriorated.

(57) (Yield Strength: 460 to 550 MPa)

(58) (Tensile Strength: 550 to 740 MPa)

(59) Yield strength of the base metal of the steel sheet pile according to the present embodiment is 460 MPa or more in order to obtain an effect of decreasing plate thickness due to high-strengthening. In addition, tensile strength of the base metal of the steel sheet pile according to the present embodiment is 550 MPa or more in order to obtain the effect of decreasing plate thickness due to high-strengthening. Setting the yield strength and the tensile strength of the base metal of the steel sheet pile to be greater than the above-described values to lower the welding costs, the transport costs, and the construction costs is advantageous in regards to economic efficiency. On the other hand, in view of securing the toughness of the base metal and the weld portion of the steel sheet pile and enhancing weldability due to reducing the amount of alloys, it is preferable that the upper limit of the yield strength is 550 MPa and the upper limit of the tensile strength is 740 MPa. Such yield strength and tensile strength can be obtained when the steel sheet pile includes the above-described predetermined amount of alloys and the structure thereof becomes the predetermined state.

(60) Next, a method for manufacturing the steel sheet pile according to the present embodiment will be described. The method for manufacturing a steel sheet pile according to the present embodiment includes: heating a steel slab, which includes C:0.05 to 0.18%, Si:0.10 to 0.50%, Mn:0.50 to 1.50%, Nb:0.040 to 0.050%, V:0.20 to 0.30%, Cu:0 to 0.40%, Ni:0 to 1.00%, Mo:0 to 1.00%, Cr:0 to 1.00%, Al: limited to less than 0.05%, and remainder including Fe and impurities and of which a carbon equivalent CE.sub.N is 0.260 to 0.500, to 1100 to 1350 C.; hot-rolling the steel slab under a condition in which a cumulative reduction at a region of 900 C. or more is 90% or more and a finishing temperature is 850 C. or more to obtain the steel sheet pile; and cooling the steel sheet pile. In the method for manufacturing a steel sheet pile according to the present embodiment, the chemical composition of the steel slab may include, in terms of mass %, one or more of Cu:0.05 to 0.40%, Ni:0.10 to 1.00%, Mo:0.10 to 1.00%, and Cr:0.10 to 1.00%.

(61) In steel making, a chemical composition of a molten metal is controlled, and then the molten metal is casted to obtain the steel slab in an ordinary method. In view of productivity, the casting is preferably continuous casting. In addition, a thickness of the steel slab is preferably 200 mm or more in view of productivity, and the thickness of the steel slab is preferably 350 mm or less in view of the amount of time required for reducing segregation and for heating.

(62) The steel sheet pile according to the present embodiment is manufactured by hot-rolling the steel slab. After the hot-rolling, the slab may be air-cooled, however, accelerated cooling can be applied in order to increase the strength and the toughness of the base metal and the weld portion of the steel sheet pile.

(63) (Heating Temperature of Steel Slab Before Hot-Rolling: 1100 to 1350 C.)

(64) The heating temperature of the steel slab before hot-rolling is 1100 C. or more. If the heating temperature is too low, the temperature of the steel slab falls during the hot-rolling, and thus, a deformation resistance of the steel slab excessively increases. On the other hand, if the heating temperature of the steel slab before the hot-rolling is higher than 1350 C., a load on a heating apparatus increases as well as the amount of scale which forms on a surface of the steel slab increases. Therefore, an upper limit of the heating temperature of the steel slab before the hot-rolling is 1350 C.

(65) (Cumulative Reduction at a Region of 900 C. or More: 90% or More)

(66) After heating the steel slab, hot-rolling is performed. In the hot-rolling, a cumulative reduction at a region of 900 C. or more is 90% or more. The hot-rolling condition can increase productivity and can prevent a roll from cracking due to reducing a load on the roll. If the cumulative reduction at the region of 900 C. or more is less than 90%, the total number density of the Nb carbonitride and the V carbonitride becomes less than 0.10 pieces/m.sup.2, and the area ratio of the Widmansttten ferrite becomes less than 1%. Thereby, coarsening of the ferrite and the pearlite occurs. The structure of the ferrite and the pearlite is miniaturized by increasing reduction in a lower-temperature-side of the range of 900 C. or more, and thus, the strength and the toughness of the base metal and the weld portion of the steel sheet pile can be further increased.

(67) Typically, a cumulative reduction is a percentage of the amount of cumulative reduction (difference between a plate thickness before inputting into a first pass and a plate thickness after outputting from a last pass) with respect to a plate thickness at starting of rolling (i.e. the plate thickness just before inputting into the first pass of rolling apparatus). On the other hand, the cumulative reduction at the region of 900 C. or more can be obtained by the following expression.
r.sub.900=(t.sub.0t)/t.sub.0100(Expression 3)

(68) In the expression 3, r.sub.900 represents the cumulative reduction at the region of 900 C. or more, t.sub.0 represents a plate thickness at starting rolling, and t represents a plate thickness just before inputting into a rolling pass which starts rolling in a state in which a temperature of the steel slab is less than 900 C.

(69) Increasing a reduction in a lower-temperature-side of the range of 900 C. or more represents setting a reduction of a pass having a relatively low temperature among passes performing rolling at the range of 900 C. or more (specially, a reduction of a pass performing rolling at a range of 900 to 1000 C.) to be larger than a reduction at a pass having a relatively high temperature (specially, a reduction at a pass performing rolling at a range of 1000 C. or more).

(70) (Finishing Temperature: 850 C. or More)

(71) A finishing temperature of the hot-rolling is 850 C. or more. If the hot-rolling is performed in less than 850 C., since ferrite transformation already starts, the hot-rolling becomes dual phase rolling. If the dual phase rolling is performed, a worked ferrite forms, and thus, the toughness of the base metal is deteriorated and the load on the roll increases due to increasing of the deformation resistance.

(72) The steel sheet pile obtained by the hot-rolling is cooled. The method for cooling is not limited. For example, when the steel sheet pile which is hot-rolled as described above is cooled as a typical method for manufacturing a typical steel sheet pile, the steel sheet pile including 70 area % or more in total of the ferrite and the pearlite, 1 area % or more of the Widmansttten ferrite, and the precipitate can be obtained.

EXAMPLES

(73) Steel slabs having chemical compositions disclosed in Table 1 were manufactured by continuous casting. Steel sheet piles of which thickness of web was 10.8 mm were manufactured by heating the steel slabs obtained thereby in a furnace, and then hot-rolling. Manufacturing conditions therein are disclosed in Table 2. Tensile tests were performed on 14 B test pieces defined in JIS Z 2241 and collected from web width portions (W) in the steel sheet piles obtained thereby. In addition, Charpy impact tests were performed on test pieces in accordance with JIS Z 2242 collected from above-described locations. The Charpy impact test pieces were subsize test pieces (i.e. test pieces having height of 10 mm and width of 7.5 mm). When a Charpy absorbed energy (impact value) obtained by performing the Charpy impact test was higher than a desired value, it was determined that the toughness was good. Regarding mechanical property, a desired value of the yield strength YP is 460 MPa or more, a desired value of the tensile strength TS is 550 MPa or more, and a desired value of the impact value is 32 J or more.

(74) In addition, samples were collected from the w portions, structures thereof were observed by optical microscope to confirm structure, and average grain sizes of the structures were measured. Furthermore, observing samples of extraction replica was performed by using TEM to obtain total number densities of the Nb carbonitrides and the V carbonitrides in the structures. Measuring the average grain size of the structure and the total number density of the Nb carbonitride and the V carbonitride in the structure was performed in an area of 10 m square. The results are disclosed in Table 2.

(75) No. 1 to No. 12 were examples and satisfied quality of material. The structures of the examples were mainly constructed by the ferrite, the pearlite, and the Widmansttten ferrite and the area ratios of the Widmansttten ferrite thereof were 1% or more as far as the above-described observing the structure. On the other hand, No. 13 to No. 27 were comparative examples and the strengths and/or the Charpy absorbed energies thereof did not reach to the desired values. No. 13, 26, 15, 17, 19, and 21 included small amounts of C, Si, Mn, Nb, and V, respectively, and therefore, the yield strengths thereof did not satisfy the desired value. No. 14, 16, 18, 20, 22, and 23 included excessive amounts of C, Si, Mn, Nb, V, and Al, respectively, and therefore, the toughnesses thereof were deteriorated. No. 24 had low toughness, since CE.sub.N thereof was excessive. No. 25 had low impact value, since CE.sub.N thereof was insufficient. No. 27 had low impact value, since the heating temperature before rolling thereof was insufficient, and thus, the Widmansttten ferrite did not form.

(76) TABLE-US-00001 TABLE 1 Steel CHEMICAL COMPOSITION (mass %) No. C Mn Si Nb Al V Cu Ni Mo Cr CE.sub.N MAIN STRUCTURES REMARKS 1 0.16 1.18 0.23 0.040 0.02 0.20 0.393 FERRITE-PEARLITE- EXAMPLES WIDMANSTTTENFERRITE 2 0.16 1.17 0.23 0.040 0.02 0.30 0.410 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 3 0.07 1.50 0.40 0.047 0.02 0.20 0.50 0.261 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 4 0.17 0.90 0.22 0.040 0.02 0.21 0.367 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 5 0.15 1.30 0.12 0.040 0.02 0.20 0.388 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 6 0.09 1.30 0.48 0.040 0.02 0.22 0.268 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 7 0.17 0.50 0.30 0.040 0.02 0.20 0.305 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 8 0.16 1.18 0.23 0.040 0.04 0.21 0.395 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 9 0.09 1.30 0.48 0.040 0.02 0.20 0.40 0.265 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 10 0.08 1.20 0.48 0.040 0.02 0.21 0.95 0.265 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 11 0.07 1.30 0.47 0.040 0.02 0.20 0.40 0.274 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 12 0.08 1.21 0.48 0.040 0.02 0.22 0.20 0.263 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 13 0.03 1.50 0.45 0.040 0.02 0.20 0.193 FERRITE-PEARLITE- COMPARATIVE WIDMANSTTTENFERRITE EXAMPLES 14 0.19 1.01 0.21 0.040 0.02 0.20 0.409 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 15 0.15 1.20 0.07 0.040 0.02 0.20 0.372 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 16 0.16 1.18 0.53 0.040 0.02 0.20 0.404 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 17 0.16 0.45 0.23 0.040 0.02 0.20 0.281 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 18 0.16 1.59 0.23 0.040 0.02 0.20 0.455 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 19 0.11 1.18 0.23 0.031 0.02 0.20 0.287 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 20 0.10 1.17 0.23 0.053 0.02 0.20 0.267 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 21 0.16 1.18 0.23 0.040 0.02 0.15 0.384 FERRITE-PEARLITE 22 0.16 1.18 0.23 0.040 0.02 0.32 0.415 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 23 0.16 1.18 0.23 0.040 0.07 0.20 0.393 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 24 0.18 1.49 0.45 0.050 0.02 0.29 0.501 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 25 0.05 1.49 0.49 0.040 0.04 0.20 0.35 0.254 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 26 0.04 1.49 0.49 0.040 0.04 0.20 0.60 0.267 FERRITE-PEARLITE- WIDMANSTTTENFERRITE 27 0.16 1.18 0.23 0.040 0.02 0.20 0.393 FERRITE-PEARLITE A BLANK COLUMN MEANS THAT AN ELEMENT REGARDING THERETO IS NOT DELIBERATELY INCLUDED. AN UNDERLINED VALUE IS OUT OF RANGE OR THE PRESENT INVENTION.

(77) TABLE-US-00002 TABLE 2 CUMU- TOTAL NUMBER LATIVE AVERAGE DENSITY OF Nb HEATING REDUCTION FINISHING GRAIN SIZE OF CARBONITRIDE TEMPER- AT A REGION TEMPER- ELON- FERRITE AND AND V Steel ATURE OF 900 C. ATURE YP TS GATION IMPACT PEARLITE CARBONITRIDE No. C. OR MORE % C. MPa MPa % VALUE J m picces/m.sup.2 REMARKS 1 1300 90 860 490 630 17 50 13 0.15 EXAMPLES 2 1300 93 880 494 635 16 45 12 0.27 3 1250 97 910 467 559 18 78 31 0.11 4 1250 97 890 481 620 18 60 17 0.15 5 1250 97 890 495 639 16 45 13 0.16 6 1250 97 900 464 571 19 112 70 0.12 7 1250 97 890 474 610 18 117 30 0.20 8 1330 97 910 480 618 18 69 20 0.15 9 1280 97 890 468 577 19 113 65 0.13 10 1150 97 900 465 570 19 111 51 0.12 11 1280 97 900 482 619 19 70 20 0.11 12 1280 97 890 478 615 18 100 21 0.11 13 1300 97 900 440 568 20 72 85 0.08 COMPARATIVE 14 1250 97 910 495 630 14 30 11 0.20 EXAMPLES 15 1250 97 870 435 555 21 32 89 0.15 16 1300 97 880 490 630 15 27 14 0.15 17 1300 97 910 455 585 19 28 90 0.17 18 1280 90 860 498 631 16 31 20 0.16 19 1280 93 870 454 582 17 70 26 0.13 20 1280 97 860 495 629 16 21 19 0.26 21 1300 97 890 453 578 17 80 38 0.11 22 1250 93 870 498 640 15 20 12 0.32 23 1300 97 870 478 620 15 30 42 0.15 24 1250 90 850 497 625 15 19 13 0.16 25 1280 97 860 455 629 16 69 30 0.25 26 1280 97 860 456 630 16 70 31 0.26 27 1050 97 840 461 570 16 30 85 0.09 AN UNDERLINED VALUE IS OUT OF RANGE OR THE PRESENT INVENTION.

INDUSTRIAL APPLICABILITY

(78) According to the present invention, a high-strength steel sheet pile in which alloys are not excessively included, productivity is enhanced and mill roll is prevented from cracking by rolling at high temperature, a yield stress is 460 MPa or more, a tensile strength TS is 550 MPa or more, and an impact value is 32 J or more and a manufacturing method thereof can be provided, and therefore, the present invention remarkably contributes to the industry.