JP2009256780A - 780 MPa CLASS LOW YIELD RATIO CIRCULAR STEEL PIPE FOR BUILDING STRUCTURE HAVING EXCELLENT EARTHQUAKE RESISTANCE, AND METHOD FOR PRODUCING THE SAME - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a circular steel pipe having tensile strength in a class of 780 MPa lying in the highest class in application for a building steel frame, in which the consistence of high strength and a low yield ratio is achieved, and further, the hardness on the outer face side of the steel pipe caused by bending upon steel pipe forming is reduced, thus its ductility is secured and jointly, cracking resistance caused by welding is improved, so as to contribute to the improvement of earthquake resistance. <P>SOLUTION: In the circular steel pipe, a chemical componential composition is regulated while satisfying prescribed relational formula, and further, the following requirements (A) to (C) are satisfied: (A) the average Vickers hardness Hv in the central part other than the surface layer part from the surface/back surface of the steel pipe to a depth of 2 mm is 230 to 310; (B) in the microstructure of the steel pipe, the fraction of a bainitic ferritic phase is ≥80 area% and the fraction of a martensitic phase is ≤5 area%; and (C) the average Vickers hardness Hv in the surface layer part from the surface/back surface of the steel pipe to a depth of 2 mm is ≤1.3 times the average Vickers hardness Hv in the central part. <P>COPYRIGHT: (C)2010,JPO&INPIT

Description

  TECHNICAL FIELD The present invention relates to a circular steel pipe for architectural steel frame applications that mainly requires earthquake resistance, and a method for producing the same, and in particular, a high tensile strength of 780 MPa or more (780 MPa class) and a yield ratio of 90% or less. It relates to a high strength low yield ratio round steel pipe and a useful method for producing such a round steel pipe.

  The ratio of yield stress YS to tensile strength TS (YS / TS) under the idea that building steels absorb seismic energy by plastic deformation after elastic deformation in order to ensure the earthquake resistance of building structures. The upper limit of the yield ratio YR indicated by

  Since circular steel pipes applied to building structures as described above are formed by press bending or the like of steel sheets, material changes due to work hardening occur, yield ratio YR and steel pipe front and back hardness increase. Toughness decreases. In particular, the outer surface side of a round steel pipe formed by a strong bending process such that the ratio (D / t) of the diameter D of the round steel pipe to the thickness t of the steel pipe is 20 or less is harder than the thickness center portion. Since there is a large increase in the tensile stress field, there is a risk of brittle fracture due to a decrease in ductility.

  That is, when deformed by receiving a load in the event of a large earthquake, cracks are likely to occur from the outer surface side, and the circular steel pipe has an inherent problem that does not occur in a four-sided box column. In particular, when an attached mold or the like is welded to a circular steel pipe, the hardened part of the heat-affected zone (HAZ) becomes the starting point of brittle fracture, and further, the ductile decrease in the ductility of the outer peripheral surface of the circular steel pipe can cause and propagate brittle fracture. It becomes a problem.

  By the way, as a method of manufacturing a steel pipe by cold forming, in addition to a UOE forming method (Uing press-Oing press-expander method) applied to a steel pipe for a line pipe, a press bend cold forming method (hereinafter, simply “ The “press bend method” is sometimes used. Among the above forming methods, when the steel plate thickness is large (for example, plate thickness: more than 30 mm) and strong bending work is required, the press bend method is adopted.

  The press bend method is a method in which a part (straight portion) of a steel plate is stamped and bent, and the stamping position is sequentially moved to form a circle, which has a high processing capability. When a circular steel pipe is formed by such a press bend method, the hardening of the outer surface of the circular steel pipe is particularly remarkable. As a method for reducing such hardness, a stress-annealing annealing is performed after forming the steel pipe in a 590 MPa class steel pipe. (Stress Relieving: hereinafter referred to as “SR heat treatment”) is known to be performed.

  However, in the case of a 780 MPa class steel pipe, on the premise that SR heat treatment is applied, when a steel sheet having a conventional tensile strength TS: 780 MPa or more is applied, the amount of alloy elements added is large, so martensite, lower bainite, etc. In addition to ensuring the characteristics of the low yield ratio YR (hereinafter sometimes referred to as “low YR characteristics”) when this hard structure is the main component, the steel pipe is also subjected to SR heat treatment. It is very difficult to secure the base material toughness, and the hardness of the steel pipe surface is still hard. On the other hand, in order to reduce the hardness of the steel pipe surface, if the SR heat treatment temperature is increased, the hardness of the steel pipe thickness central portion is also reduced, and the tensile strength TS: 780 MPa or more, which is a required strength as a circular steel pipe, is ensured. Was difficult.

  In addition to the mechanical properties such as high strength and low yield ratio characteristics, it is also important for building materials to ensure high heat input welding characteristics and good weldability to reduce construction costs. Unnecessarily, alloying elements cannot be added.

  Various techniques have been proposed for the steel pipe as described above. For example, Patent Document 1 proposes a method for producing a press-bend cold-formed circular steel pipe of 490 MPa or more. Although this technique is useful as a technique of a 490 MPa class circular steel pipe, the Vickers hardness Hv in the surface layer portion from the front and back surfaces of the steel pipe to a depth of 1 mm is about 140 to 200, and the thickness of the steel pipe Since the hardness of the central portion is further reduced, a tensile strength TS of 780 MPa or more cannot be obtained.

Patent Document 2 discloses a thick steel plate having a main structure of ferrite and a hard second phase fraction of 10 to 70%. With this technique, the tensile strength TS: 780 MPa or more cannot be stably secured from the structure. With respect to the production method, it is difficult to ensure the stability of the hard phase only by the provision of “cooling stop temperature of 500 ° C. or less”, and the rolling end temperature: the Ar ₃ transformation point or higher, which is the main point of the structure control, and the cooling rate : 5 ° C./second or less, and a uniform metal structure and hardness cannot be stably obtained in the thickness direction.

Patent Document 3, using the steel material was appropriately adjusted chemical composition, the rolling end temperature subjected to hot rolling to a temperature range of not lower than Ar ₃ transformation point, then, from the temperature range of not lower than Ar ₃ transformation point after quenching into 300 ° C. or less, Ac ₁ ~Ac ₁ + 150 upon reheating ° C. to the temperature range, the heating rate up to the reheating temperature is below 1 ° C. / sec and Ac ₁ ~Ac ₁ + 150 at ° C. temperature range of Has been proposed for producing a high-strength, high-toughness steel such that the dwell time is 90 seconds or less.

  However, this technology does not take into account the metal structure and the hardness distribution in the thickness direction, and when press bending is performed, the hardness of the outer surface cannot be suppressed, and when a round steel pipe is formed It is expected that good earthquake resistance will not be demonstrated. In addition, in the manufacturing method, there is a problem that a uniform structure cannot be obtained in the plate thickness direction because rapid heating and residence time in the two-phase region are short.

  On the other hand, Patent Document 4 proposes a method for producing a high-strength thick steel plate for a building structure that is excellent in super large heat input HAZ toughness. This technique is a technique for ensuring good HAZ toughness when super-high heat input welding is performed as a building structure. However, in this technique, the target steel plate is basically of low strength (700 MPa or less), the hardness distribution in the thickness direction is not taken into consideration, the C content is relatively high, and the rolling temperature Since the hardness of the outer surface becomes high in a round steel pipe after being formed by the press bend method, good earthquake resistance cannot be exhibited.

  Patent Document 5 proposes a high-strength steel pipe material having a low surface hardness and yield ratio after pipe making. In this technique, the strength of the steel pipe material is set to 780 MPa class, but it is difficult to stably obtain a strength of 780 MPa or more from the component system. In addition, in the production method, no two-phase region quenching temperature is defined, and a uniform metal structure and hardness cannot be obtained in the thickness direction.

  Patent Document 6 discloses a method for producing a high-strength, high-toughness steel plate having a uniform hardness distribution in the thickness direction. In this technology, by applying a special manufacturing method in which water is cooled once in the middle of rolling, reheated and then rolled again, fine processed ferrite is generated in the surface layer portion, and the hardness of the surface is reduced. In this case, the hardness distribution in the thickness direction is made uniform.

  However, with this technique, there is a possibility that the surface layer portion may be softer than the inside of the plate thickness, and there is a problem that it is difficult to manage production in terms of mass production in order to obtain a stable material. In this technique, the hardness after being processed into a circular steel pipe is not taken into consideration.

JP 2007-270304 A JP 2003-3229 A JP 2006-283187 A JP 2005-68519 A JP 2003-293075 A JP-A-5-148544

  The present invention has been made under such circumstances, and its purpose is to achieve both high strength and low yield ratio for steel pipes with a tensile strength TS: 780 MPa class, which is located in the highest strength class for building steel frame applications. By reducing the hardness of the outer surface of the steel pipe caused by bending during steel pipe forming, the ductility is ensured, and at the same time, the crack resistance when welding to the outer surface is improved. It is an object of the present invention to provide a circular steel pipe that can contribute to improvement in performance and a useful method for manufacturing such a circular steel pipe.

  The circular steel pipe of the present invention that can achieve the above-mentioned object is C: 0.01 to 0.06% (meaning of mass%, the same applies hereinafter), Si: 0.10 to 0.40%, Mn: 1. 60 to 2.50%, Al: 0.025 to 0.090%, Cu: 0.15 to 0.70%, Ni: 0.90 to 1.60%, Cr: 0.50 to 1.35% , Mo: 0.10 to 0.30%, Ti: 0.008 to 0.025%, B: 0.0005 to 0.0025%, N: 0.0030 to 0.0060% and Ca: 0.0005 -0.0040%, respectively, and the PCM value represented by the following formula (1) is 0.30% or less, and the balance is composed of Fe and unavoidable impurities. 012% or less (excluding 0%), S: 0.005% or less (not including 0%), and O: 0.00 Each was suppressed to 0% or less (not including 0%), and has a gist and a point which satisfies the following requirements (A) ~ (C).

PCM value = [C] + [Si] / 30 + [Mn] / 20 + [Cu] / 20 + [Ni] / 60 + [Cr] / 20 + [Mo] / 15 + [V] / 10 + ([B] × 5) (1)
However, [C], [Si], [Mn], [Cu], [Ni], [Cr], [Mo], [V] and [B] are respectively C, Si, Mn, Cu, Ni, Content (mass%) of Cr, Mo, V, and B is shown.
(A) The average Vickers hardness Hv of the central part excluding the surface layer part from each of the front and back surfaces of the steel pipe to a depth of 2 mm is 230 to 310.
(B) In the microstructure of the steel pipe, the fraction of bainitic ferrite phase is 80 area% or more, and the fraction of martensite phase is 5 area% or less.
(C) The average Vickers hardness Hv of the surface layer portion from each of the front and back surfaces of the steel pipe to a depth of 2 mm is 1.3 times or less of the average Vickers hardness Hv of the central portion.

  In producing the circular steel pipe as described above, the slab made of the chemical component is heated to 950 to 1200 ° C., and then hot rolled at a finish rolling temperature in the range of 800 to 930 ° C. to obtain a predetermined plate thickness. Then, it is cooled with water until the surface temperature becomes 350 ° C. or less at a cooling rate of 2 to 25 ° C./second at a position of t / 4 (t: plate thickness), and then re-entered within the range of temperature: 700 to 900 ° C. It is only necessary to perform a quenching treatment by heating, tempering in a temperature range of 450 to 700 ° C. to form a steel plate, and forming the steel plate into a circular steel pipe by a press bend method using the obtained steel plate.

  According to the present invention, the chemical composition of the steel sheet (the steel sheet constituting the steel pipe) is appropriately adjusted, the area fraction of each phase in the microstructure is appropriately controlled, and the hardness distribution in the thickness direction is controlled. By making it appropriate, it is possible to achieve both high strength of 780 MPa or more and a low yield ratio, reduce the hardness on the outer surface side of the steel pipe due to bending during steel pipe forming, and ensure ductility, and also by welding By improving crack resistance, a round steel pipe that can contribute to improved earthquake resistance was realized.

  The present inventors have studied from various angles in order to achieve both a high strength of 780 MPa or more and a low yield ratio, and to reduce the hardening of the outer surface of the circular steel pipe caused by work hardening during press bending. did. As a result, as a basic microstructure of the steel pipe (ie, steel plate), the bainitic ferrite phase fraction (area fraction) is set to 80% or more, and the martensite phase area fraction is set to 5% or less. It was found that [Requirement (B)] is important. Here, the bainitic ferrite phase is a phase of a low C bainite structure that transforms at a lower temperature than ferrite, and includes a granular bainitic ferrite structure, broad upper bainite structure, lower bainite structure, and the like. Ferrite structure and grain boundary ferrite structure are not included (for example, “Steel Bainite Photobook-1”: Japan Iron and Steel Institute Bainite Research and Study Group, 1992). Further, the martensite phase includes MA (Martensite-Austenite Constituent).

  The low-C bainitic ferrite structure is deformed because it has less carbide and less cooling rate dependence, so the hardness in the thickness direction of the steel sheet is high and the dislocation density is higher than normal polygonal ferrite. The amount of work hardening with respect to strain is reduced. For this reason, it contributes to uniform hardness distribution in the thickness direction after making the steel pipe. When the area fraction of the bainitic ferrite phase is less than 80% and the area fraction of the hard phase such as martensite is increased, the hardness on the outer surface side of the circular steel pipe is increased, the deformability is deteriorated, and the elongation at break is lowered. It will be. For these reasons, the area fraction of bainitic ferrite needs to be at least 80% or more, preferably 85% or more.

  On the other hand, for the martensite phase, it is necessary to suppress the area fraction to 5% or less from the viewpoint of securing steel pipe (steel plate) toughness. That is, when the area fraction of the martensite phase exceeds 5%, the hard martensite becomes a starting point of fracture, resulting in a disadvantage that the toughness is remarkably deteriorated. In addition, although the microstructure of the circular steel pipe of this invention should just be controlled as mentioned above, a bainite phase, a ferrite phase, etc. may be partially contained as the remainder.

  In order to obtain the microstructure as described above, it is necessary to appropriately control the manufacturing conditions, but as a premise, it is also necessary to appropriately control the chemical composition of the steel sheet. The basic direction is to reduce the surface hardness of the circular steel pipe by reducing the C content, and to maintain high strength and low yield ratio on the premise of this, the baiini by appropriate addition of Cr. It is effective to utilize the strengthening mechanism by the formation of tick ferrite, the strengthening by solid solution of Cu and Ni in the bainitic ferrite, and the ferrite transformation control from the austenite grain boundary by B.

  An effective means for improving the strength of the steel sheet is to increase the amount of alloying elements. In particular, in order to achieve a high strength of 780 MPa class, it is necessary to use a relatively large amount of alloy elements and use various strengthening mechanisms. However, such an increase in alloy elements leads to deterioration of weldability such as crack resistance and mechanical properties of welded joints. The present inventors have found that by adding an appropriate alloy element and optimizing the content thereof, both high strength and low YR characteristics can be achieved and work hardening by bending can be reduced.

  By satisfying the above requirements (microstructure and chemical composition), the hardness distribution in the sheet thickness direction is made uniform, the work hardening amount is stabilized, and the area up to 2 mm below the outer surface of the circular steel pipe (steel sheet surface) Since the ratio of Vickers hardness Hv of the steel layer thickness direction center part [t / 2 part (t: plate thickness)] and the steel pipe thickness direction center part can be suppressed, and the earthquake resistance as a circular steel pipe can be improved. is there.

  From the above viewpoint, the chemical composition of the circular steel pipe of the present invention has been determined. The reasons for limiting the range of each element including the above-described alloy components (C, Cr, Ni, B) will be described. In the present invention, as described above, C: 0.01 to 0.06%, Si: 0.10 to 0.40%, Mn: 1.60 to 2.50%, Al: 0.025 to 0.5. 090%, Cu: 0.15 to 0.70%, Ni: 0.90 to 1.60%, Cr: 0.50 to 1.35%, Mo: 0.10 to 0.30%, Ti: 0 0.008-0.025%, B: 0.0005-0.0025%, N: 0.0030-0.0060% and Ca: 0.0005-0.0040%, respectively, and (1) Although it is necessary to control the PCM value represented by the formula within an appropriate range, the reasons for limiting the ranges of these elements are as follows.

[C: 0.01 to 0.06%]
C has an effect of increasing the strength of the steel sheet, is an element important for controlling the hardness, and is an element that deteriorates weldability such as crack resistance. If the C content is less than 0.01%, the required base material (steel pipe) strength cannot be ensured. However, if the C content exceeds 0.06%, the hardness distribution in the thickness direction becomes large due to the martensitic transformation of the surface layer portion. In addition, island-like martensite (MA) is excessively generated in the welded portion, the HAZ becomes too hard, and cracks are likely to occur, which becomes a point of occurrence of destruction during an earthquake. In addition, the preferable minimum of C content is 0.02%, and a preferable upper limit is 0.05%.

[Si: 0.10 to 0.40%]
Si is an element effective for improving the strength of a steel pipe. In order to exhibit such a strengthening mechanism, it is necessary to contain Si by 0.10% or more. However, if the Si content is excessive, the base material toughness, the HAZ toughness and the weldability deteriorate, so the content is made 0.40% or less. In addition, the minimum with preferable Si content is 0.15%, and a preferable upper limit is 0.35%.

[Mn: 1.60 to 2.50%]
Mn is an element effective in improving hardenability and ensuring strength and toughness. In order to exhibit such an effect, it is necessary to contain Mn 1.60% or more. However, if Mn is contained excessively, toughness deteriorates, so the upper limit is made 2.50%. In addition, the minimum with preferable Mn content is 1.80%, and a preferable upper limit is 2.20%.

[Al: 0.025 to 0.090%]
Al is an element necessary for ensuring the hardenability of B by deoxidation and fixation of free nitrogen. In order to exert these effects, it is necessary to contain 0.025% or more. However, if excessively contained, alumina-based coarse inclusions are formed and the base material toughness is lowered. It is necessary to do the following. In addition, the minimum with preferable Al content is 0.035%, and a preferable upper limit is 0.080%.

[Cu: 0.15 to 0.70%]
Cu is an element useful for improving the base material strength by solid solution strengthening. In order to exhibit such an effect, it is necessary to contain 0.15% or more of Cu. However, if the Cu content is excessive, Cu cracking may occur at the time of gas cutting, so it is necessary to be 0.70% or less. In addition, the minimum with preferable Cu content is 0.25%, and a preferable upper limit is 0.65%.

[Ni: 0.90 to 1.60%]
Ni is an element that is effective in improving base metal toughness / HAZ toughness and improving hardenability to improve strength and also preventing Cu cracking and weld cracking. In order to exhibit such an effect, Ni needs to be contained by 0.90% or more. However, if the Ni content is excessive, the weld crack resistance deteriorates and scale flaws are likely to occur during rolling, so it is necessary to make it 1.60% or less. In addition, the minimum with preferable Ni content is 1.10%, and a preferable upper limit is 1.35%.

[Cr: 0.50 to 1.35%]
Cr is an element effective for improving the hardenability and improving the strength. In order to exert such an effect, it is necessary to contain 0.50% or more of Cr. However, if the Cr content is excessive, the weld crack resistance deteriorates, so it is necessary to make it 1.35% or less. In addition, the minimum with preferable Cr content is 0.60%, and a preferable upper limit is 1.25%.

[Mo: 0.10 to 0.30%]
Mo is an element that improves hardenability and improves strength, and is an element that easily generates carbides. In order to exert the effect of improving the hardenability by Mo, Mo needs to be contained by 0.10% or more. However, if the Mo content becomes excessive, the hardenability becomes excessive and the weld crack resistance deteriorates, so it is necessary to make it 0.30% or less. In addition, the minimum with preferable Mo content is 0.15%, and a preferable upper limit is 0.25%.

[Ti: 0.008 to 0.025%]
Ti is an element that forms N and nitride (TiN) to prevent coarsening of austenite grains (γ grains) during heating before hot rolling, and is effective in improving toughness. Further, fixing N is effective in securing the hardenability of B. In order to exert these effects, it is necessary to contain Ti by 0.008% or more. However, if the Ti content is excessive, TiN becomes coarse and the base material toughness deteriorates, so it is necessary to make it 0.025% or less. In addition, the minimum with preferable Ti content is 0.010%, and a preferable upper limit is 0.018%.

[B: 0.0005 to 0.0025%]
Free B exists at the γ grain boundary and is an effective element for improving the hardenability and improving the strength of the base material. If the B content is less than 0.0005%, the effect of improving the strength of the base material is small, and a tensile strength of 780 MPa or more cannot be secured. However, if the B content is excessive, inclusions are generated and the base material toughness deteriorates, so it is necessary to make the content 0.0025% or less. In addition, the minimum with preferable B content is 0.0008%, and a preferable upper limit is 0.0020%.

[N: 0.0030 to 0.0060%]
N is an element effective for producing TiN, preventing coarsening of γ grains during heating and hot welding before hot rolling, and improving base metal toughness and HAZ toughness. If the N content is less than 0.0030%, TiN is insufficient, the heated γ grains become coarse, and the toughness deteriorates. Therefore, it is necessary to contain 0.0030% or more. On the other hand, if the N content becomes excessive and exceeds 0.0060%, the toughness of the steel pipe deteriorates due to embrittlement caused by bending. In addition, the minimum with preferable N content is 0.0035%, and a preferable upper limit is 0.0055%.

[Ca: 0.0005 to 0.0040%]
Ca is an element effective for detoxifying the weld cracking resistance by spheroidizing MnS. In order to exhibit such an effect, Ca needs to be contained by 0.0005% or more. However, when the Ca content exceeds 0.0040% and becomes excessive, inclusions are coarsened and the base metal toughness is deteriorated. In addition, the minimum with preferable Ca content is 0.0015%, and a preferable upper limit is 0.0030%.

[PCM value: 0.30% or less]
The PCM value represented by the formula (1) is the most common requirement as an index for preventing cold cracking due to welding. In order to prevent weld cracking, the PCM value needs to be 0.30% or less. The PCM value is preferably 0.28% or less.

  In the circular steel pipe of the present invention, in addition to the above components, it consists of Fe and unavoidable impurities (for example, P, S, O, etc.), but there are also trace components (allowable components) that are inevitably mixed during melting. Such circular steel pipes are also included in the scope of the present invention. However, P, S, O, etc. as inevitable impurities need to be controlled within the following ranges from the following viewpoints.

[P: 0.012% or less (excluding 0%)]
P, which is an unavoidable impurity, adversely affects the toughness of the base metal and the welded portion. Even without causing such inconvenience, the content must be suppressed to 0.012% or less. It should be 010% or less.

[S: 0.005% or less (excluding 0%)]
Since S forms MnS and degrades weld crack resistance, it is preferable that S be as small as possible. From such a viewpoint, the S content needs to be suppressed to 0.005% or less, and preferably 0.003% or less.

[O: 0.0040% or less (excluding 0%)]
O combines with various elements to form oxides. In some cases, the oxide becomes coarse and causes the base material toughness to deteriorate. From this point of view, the O content needs to be 0.0040% or less, and if the content is excessive, the oxide becomes coarse. Preferably, the content is suppressed to 0.0030% or less.

  In the circular steel pipe of the present invention, the average Vickers hardness Hv of the central part excluding the surface layer part from the front and back surfaces (front and back surfaces of the steel plate constituting the steel pipe) to a depth of 2 mm is 230 to 310. It is also necessary [Requirement (A) above]. This Vickers hardness Hv correlates with the tensile strength TS, and in order to obtain the desired tensile strength TS and yield ratio YR, it is also necessary that the average Vickers hardness Hv at the center of the steel pipe thickness is 230 to 310. It is. The average Vickers hardness Hv at this time is a continuous measurement of the hardness from the position of 4 mm depth from the surface of the steel pipe thickness section to the position of 4 mm from the back surface in the direction of the back surface at intervals of 2 mm. Averaged. If the average Vickers hardness Hv at the center of the steel pipe thickness is less than 230, the low yield ratio YR can be secured, but the tensile strength TS becomes less than 780 MPa and the strength is not satisfied. Moreover, when the average Vickers hardness Hv of the steel pipe thickness center part exceeds 310, tensile strength TS will become large too much and the yield ratio YR will also become high.

  In the circular steel pipe of the present invention, the average Vickers hardness Hv of the surface layer part from each of the front and back surfaces of the steel pipe to a depth of 2 mm is 1.3 times or less of the average Vickers hardness Hv of the steel pipe thickness center part. It is also necessary [Requirement (C) above]. The average Vickers hardness Hv of the surface layer portion is an average value of four points at positions 1 mm and 2 mm deep from the front surface and positions 1 mm and 2 mm deep from the back surface.

  If the ratio of the hardness of the surface layer to the center of the steel pipe exceeds 1.3 times, the plastic deformability of the surface layer will decrease, so the ductility of the surface layer will follow when tensile stress is applied due to a heavy load during a large earthquake. There is a risk of cracking from the surface. Furthermore, when there is accessory welding, the HAZ hardened part by welding becomes a starting point of crack generation, brittle cracks are generated and propagated in the low ductility and low toughness part of the surface layer part, and there is a possibility that the circular steel pipe breaks brittlely. The value of this ratio is preferably 1.25 times or less.

  In order to manufacture the circular steel pipe of the present invention, a slab made of the above chemical components is heated to 950 to 1200 ° C., and then hot rolled at a finish rolling temperature in the range of 800 to 930 ° C. The thickness is then changed to a thickness of t / 4 (t: thickness) at a cooling rate of 2 to 25 ° C./second until the surface temperature is 350 ° C. or lower, and then the temperature is in the range of 700 to 900 ° C. The steel plate is reheated to be tempered and tempered in a temperature range of 450 to 700 ° C. to form a steel plate. The resulting steel plate may be formed into a circular steel pipe by the press bend method, but the conditions for each step are defined. The reason is as follows.

[Heating slab to 950-1200 ° C]
This heating temperature greatly affects the structure control before hot rolling. When the heating temperature is less than 950 ° C., the rolling final pass (finish rolling) temperature is less than 800 ° C., ferrite precipitates from the surface before water cooling, and it becomes impossible to ensure the strength of the base material of 780 MPa or more and the hardness in the plate thickness direction. The distribution is not uniform. On the other hand, if the heating temperature exceeds 1200 ° C., the base material toughness deteriorates due to the coarsening of the γ grain size.

[Hot rolling is performed at a finish rolling temperature of 800 to 930 ° C. to a predetermined thickness]
For controlled cooling (accelerated cooling), prior structure control is important. For this purpose, it is necessary to manage the rolling end temperature (finish rolling temperature) and cooling start temperature in controlled rolling. When the finish rolling temperature is less than 800 ° C., ferrite precipitates before the start of cooling, and a desired strength cannot be obtained. On the other hand, when the finish rolling temperature exceeds 930 ° C., the structure before cooling becomes coarse, the base material toughness deteriorates, and the hardness distribution in the sheet thickness direction increases. The finish rolling temperature is preferably 900 ° C. or lower.

[The cooling rate at the position of t / 4 (t: plate thickness) is 2 to 25 ° C./second]
The cooling process (DQ) after rolling is an important process for controlling the structure. When the cooling rate is less than 2 ° C./second, it becomes impossible to ensure an area fraction of bainitic ferrite (bainite) which is a desired structure: 80% or more. When the cooling rate is larger, the bainitic ferrite structure is refined and the toughness is improved. However, when it exceeds 25 ° C./second, martensite (including MA) which is a harmful structure is present in the structure near the surface. It increases, the toughness of the base material deteriorates, and the strength becomes excessive and the surface hardens, so the ductility (elongation performance) decreases. Note that t / 4 (t: plate thickness) is used as a position for measuring the cooling rate because it is a position that exhibits the average performance of the steel sheet.

[Cooling stop temperature: Steel sheet surface temperature is 350 ° C or lower]
Depending on the cooling stop temperature, the form of martensite and lower bainite changes and the strength changes. When the cooling stop temperature exceeds 350 ° C., the low temperature transformation structure is reduced at the center of the plate thickness, the strength is lowered, and the transformation structure and the hardness distribution in the plate thickness direction are not uniform in the plate thickness direction. In order to uniformly transform in the plate thickness direction, the cooling stop temperature needs to be 350 ° C. or lower.

[Temperature: quenching by reheating to 700 to 900 ° C]
In order to obtain a composite structure of a soft phase and a hard phase that realizes low YR characteristics, it is an effective means to heat to a temperature in a two-phase region between Ac ₁ and Ac ₃ . For this purpose, the temperature is 700 to 900 ° C., and by heating to a temperature in the two-phase region, a part becomes a soft structure by tempering, a part reversely transforms into an austenite phase, and a hard structure is obtained by subsequent cooling. By controlling the two-phase region temperature, the area fraction and hardness of the hard phase can be changed to control YS, TS, and YR. When the reheating temperature is lower than 700 ° C., a strength of 780 MPa or more cannot be ensured. When the reheating temperature exceeds 900 ° C., the strength is high, but a low YR of 85% or less cannot be achieved. After reheating to 700 to 900 ° C., a part is reversely transformed into austenite, and the austenite phase is transformed into a hard phase as it is by subsequent quenching (water cooling). Since the structure of the hard phase and the soft phase is extremely fine, it is difficult to discriminate with an optical microscope, and the entire composite structure including the hard phase and the soft phase is defined as a bainitic ferrite (bainite) phase.

[Tempering (T) in a temperature range of 450 to 700 ° C.]
The tempering treatment is effective in reducing the strength but reducing the yield ratio YR, improving the toughness, and reducing the hardness of the surface portion. In that case, if the tempering heat treatment is in a temperature range of 450 to 700 ° C., an excessive decrease in strength can be suppressed, and an appropriate yield ratio YR and toughness can be obtained, and the surface hardness can be reduced. When the tempering temperature is less than 450 ° C., the toughness is not improved and the surface hardness is not sufficiently reduced. On the other hand, if the tempering temperature exceeds 700 ° C., the desired strength (TS, YS) cannot be obtained.

[Molded into a circular steel pipe by the press bend method]
A steel plate is cold bent by a press bending method to obtain a circular steel pipe. As described above, a steel plate having a thickness of 30 mm or less as applied to a line pipe can produce a circular steel pipe by the UOE forming method. However, a circular steel pipe for a building structure is thick and strong. Is high, it is necessary to form a circular steel pipe by a press bend method (that is, press bending). In application of such a method, D / t: Since strong processing of 10-20 is performed, the bending distortion of the surface is large and the work hardening of the surface is large. Therefore, a circular steel pipe with low surface hardness can be manufactured by performing press bending using the steel plate manufactured as described above.

[Heat treatment of round steel pipe]
After forming into a circular steel pipe, SR heat treatment may or may not be performed. According to the method of the present invention, since the strength is low, the YR is low, and the uniformity of the hardness distribution in the thickness direction of the steel pipe is excellent, the SR heat treatment is basically not necessary, but D / t ≦ 15 When the strong bending process is performed, the YR may exceed 90%. In this case, the SR heat treatment can be performed, and the heat treatment temperature is set to a temperature range of 350 to 650 ° C. Below 350 ° C., there is no YR reduction effect. On the other hand, when it exceeds 650 ° C., the decrease in YR and TS is large, and the strength of 780 MPa or more cannot be secured.

  Hereinafter, the present invention will be described in more detail by way of examples.However, the present invention is not limited by the following examples as a matter of course, and may be implemented with modifications within a range that can meet the gist of the preceding and following descriptions. Of course, they are all possible and are included in the technical scope of the present invention.

[Example 1]
Steels with the chemical composition shown in Tables 1 and 2 below are melted by a normal melting method to form steel pieces, which are then subjected to hot rolling, accelerated cooling (cooling after rolling), two-phase quenching, and tempering. A steel plate was manufactured. Using the obtained steel plate, it was formed into a circular steel pipe by the press bend method. Tables 1 and 2 also show the PCM values defined by the equation (1). The manufacturing conditions at this time are as follows.

[Production conditions]
Steel No. For 1-60, after the slab was heated to 1150 ± 50 ° C., the final rolling temperature (surface temperature) was hot rolled in the range of 900 ± 30 ° C. to obtain a sheet thickness of 60 mm, and then t / The cooling rate at the position of 4 (t: plate thickness) was controlled to 5 to 25 ° C./second, and the surface temperature when cooling was stopped was 250 ° C. or less. Furthermore, a two-phase region heat treatment (Q ′) temperature is set to 700 to 850 ° C., quenching treatment (partial air cooling) is performed, and a steel plate is tempered in a temperature range of 450 to 650 ° C., and the obtained steel plate is used by a press bend method. Molded into a round steel pipe. The bending degree at this time is 10 (t / D = 0.1) when the diameter of the circular steel pipe is D (mm) and the thickness of the steel sheet is t (mm).

  On the other hand, Steel No. About 61-64, the following conditions were changed, the steel plate was manufactured, and it shape | molded in the circular steel pipe. Steel No. No. 61, among the above conditions, the tempering temperature was 720 ° C. Steel No. No. 62, among the above conditions, the tempering temperature after quenching with a two-phase region heat treatment temperature of 930 ° C. was set to 400 ° C. Steel No. No. 63, among the above conditions, the finish rolling temperature was rolled at 750 ° C., and the reheating (Q ′) temperature after cooling was 680 ° C. Steel No. No. 64 did not perform subsequent tempering while performing the two-phase region heat treatment among the above conditions. From these steel plates, forming into a circular steel pipe was performed using steel no. Similar to 1 to 60, D / t = 10.

For each of the obtained steel tube was, while evaluating the microstructure (area fraction of each phase) and hardness of the steel tube in the following manner, the material (yield strength YS, tensile strength TS, yield ratio YR and toughness vE _{- 20} ) and weldability were evaluated by the following methods.

[Measuring method of microstructure and hardness]
By analyzing the microstructure of the microstructure, the area fractions of the bainitic ferrite phase and martensite phase were measured, and the Vickers hardness (Hv ₀ ) of the steel pipe surface layer portion and the Vickers hardness Hv ₁ of the central portion were measured (load: 98 N ) And its hardness ratio (Hv ₀ / Hv ₁ ) was determined. In this case, the hardness Hv ₀ and the hardness Hv ₁ are measured at intervals of 2 mm in the thickness direction, and the average value thereof is obtained (for example, the Vickers hardness Hv _{0 of the} surface layer portion is expressed by It becomes the average value of hardness from each of the back surface to a depth of 2 m).

[Evaluation method of yield strength YS and tensile strength TS]
A test piece of JIS Z 2201 No. 4 in the tube axis direction (corresponding to the main rolling direction of the steel plate) from the outer surface side of the circular steel pipe to the t / 4 part of the steel pipe (t is the thickness of the steel pipe: the thickness of the steel plate constituting the steel pipe). Extracted and subjected to a tensile test in accordance with JIS Z 2241. Yield stress YS (upper yield point YP or 0.2% yield strength σ _0.2 ), tensile strength TS, yield ratio YR (yield stress YS / tensile strength TS). ) Was measured. The acceptance criteria are the average values of two times, yield stress YS: 630 MPa or more, tensile strength TS: 780-930 MPa, yield ratio YR: 90% or less.

[Toughness evaluation method]
JIS Z 2204 V-notch impact test specimens are collected from the outer surface side of the circular steel pipe in the tube axis direction (the main rolling direction of the steel sheet) in t / 4 part of the steel pipe (t is the thickness of the steel pipe constituting the steel pipe). Then, a Charpy impact test was conducted in accordance with JIS Z 2242 (average value of three tests), and an average absorbed energy vE- ₂₀ at a temperature of −20 ° C. was measured. This average absorbed energy vE- ₂₀ was determined to be 47 J or more.

[Weldability (weld crack resistance)]
In accordance with the maximum hardness test of the weld heat affected zone (HAZ) defined in JIS Z 3101, a weld bead was placed on the outer surface side of the circular steel pipe, and the maximum hardness was measured. In addition, attachments were welded to the outside of the circular steel pipe, and the presence or absence of surface cracks by penetration testing and the presence of internal cracks by ultrasonic testing were investigated.

The micro composition and hardness distribution of the steel sheet (hardness and hardness ratio at the center of the steel sheet) are shown in Tables 3 and 4 below, and the materials (yield stress YS, tensile strength TS, yield ratio YR and toughness vE _-20 ) and welding. The evaluation results of the properties are shown in Tables 5 and 6 below. Tables 5 and 6 below show the maximum hardness (Hv) of HAZ as “weldability”.

  From these results, it can be considered as follows. First, steel no. 1 to 32 (Tables 1, 3, and 5) satisfy the requirements defined in the present invention, and satisfy the target values in all the characteristics (overall evaluation: ◯).

  On the other hand, Steel No. 33 to 64 (Tables 2, 4, and 6) do not satisfy any of the requirements defined in the present invention, and at least any of the required characteristics is deteriorated (overall evaluation ×).

[Example 2]
Steel No. 1 shown in Table 1 above. Steel sheets were produced under the various production conditions (DQ-Q'-T) shown in Table 7 below (Experiment No. 1) using the materials of Nos. 1 to 11 (with the chemical component composition satisfying the range specified in the present invention). 1-21). Using the obtained steel plate (plate thickness: 60 mm), it was formed into a circular steel pipe by the press bend method. About the obtained circular steel pipe, it carried out similarly to Example 1, and evaluated the material (yield stress YS, tensile strength TS, yield ratio YR, toughness vE- ₂₀ ), and weldability.

  In addition, the experiment No. Nos. 12 and 13 are those in which the slab heating temperature deviates from the range specified in the present invention. Nos. 14 and 15 are those in which the finish rolling temperature is outside the range defined in the present invention. Nos. 15 and 16 are those in which the cooling rate is outside the range defined in the present invention. No. 17 has a cooling stop temperature outside the range defined in the present invention. Nos. 18 and 19 are those in which the quenching temperature (heating temperature during quenching) is outside the range defined in the present invention. Reference numerals 20 and 21 denote tempering temperatures that are outside the range defined by the present invention.

  As is apparent from the results, it is understood that the manufacturing conditions must be appropriately controlled in order to obtain a circular steel pipe that satisfies the requirements defined in the present invention.

Claims (2)

C: 0.01-0.06% (meaning of mass%, the same applies hereinafter), Si: 0.10-0.40%, Mn: 1.60-2.50%, Al: 0.025-0. 090%, Cu: 0.15 to 0.70%, Ni: 0.90 to 1.60%, Cr: 0.50 to 1.35%, Mo: 0.10 to 0.30%, Ti: 0 0.008 to 0.025%, B: 0.0005 to 0.0025%, N: 0.0030 to 0.0060% and Ca: 0.0005 to 0.0040%, respectively, and (1) The PCM value represented by the formula is 0.30% or less, the balance is made of Fe and inevitable impurities, and P: 0.012% or less (not including 0%) of the inevitable impurities, S: 0.0. 005% or less (excluding 0%) and O: 0.0040% or less (not including 0%), respectively, One following (A) ~ (C) good architectural structural 780MPa class low yield ratio steel tube earthquake resistance which satisfies the requirements.
PCM value = [C] + [Si] / 30 + [Mn] / 20 + [Cu] / 20 + [Ni] / 60 + [Cr] / 20 + [Mo] / 15 + [V] / 10 + ([B] × 5) (1)
However, [C], [Si], [Mn], [Cu], [Ni], [Cr], [Mo], [V] and [B] are respectively C, Si, Mn, Cu, Ni, Content (mass%) of Cr, Mo, V, and B is shown.
(A) The average Vickers hardness Hv of the central part excluding the surface layer part from each of the front and back surfaces of the steel pipe to a depth of 2 mm is 230 to 310.
(B) In the microstructure of the steel pipe, the fraction of bainitic ferrite phase is 80 area% or more, and the fraction of martensite phase is 5 area% or less.
(C) The average Vickers hardness Hv of the surface layer portion from each of the front and back surfaces of the steel pipe to a depth of 2 mm is 1.3 times or less of the average Vickers hardness Hv of the central portion.   In manufacturing the round steel pipe according to claim 1, after heating the slab made of the chemical component to 950 to 1200 ° C., hot rolling is performed at a finish rolling temperature in the range of 800 to 930 ° C. The thickness is then changed to a thickness of t / 4 (t: thickness) at a cooling rate of 2 to 25 ° C./second until the surface temperature is 350 ° C. or lower, and then the temperature is in the range of 700 to 900 ° C. The steel plate was reheated and quenched, and tempered in a temperature range of 450 to 700 ° C. to form a steel plate, and the resulting steel plate was formed into a circular steel pipe by the press bend method and was excellent in earthquake resistance. Manufacturing method of 780 MPa class low yield ratio circular steel pipe for building structure.