WO2013022043A1 - 低温での衝撃エネルギー吸収特性と耐haz軟化特性に優れた高降伏比熱延鋼板およびその製造方法 - Google Patents
低温での衝撃エネルギー吸収特性と耐haz軟化特性に優れた高降伏比熱延鋼板およびその製造方法 Download PDFInfo
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- C21D9/56—Continuous furnaces for strip or wire
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12861—Group VIII or IB metal-base component
- Y10T428/12951—Fe-base component
- Y10T428/12972—Containing 0.01-1.7% carbon [i.e., steel]
Definitions
- the present invention relates to a high-yield specific hot-rolled steel sheet having a maximum tensile strength of 600 MPa or more, which is excellent in impact energy absorption characteristics at low temperatures and anti-HAZ (Heat-Affected Zone) softening characteristics, and a method for producing the same.
- This steel plate is suitable as a material for construction equipment booms and frames, as a material for trucks, automobile frames and members formed mainly by bending, and as a material for line pipes.
- Construction machinery and truck frames are assembled by forming hot-rolled steel sheets mainly by bending and arc welding the formed parts. Therefore, the material used for these parts is required to have excellent bending workability and arc weldability. In addition, since construction machinery and trucks may be used in low-temperature environments, they do not break brittlely even at low temperatures and absorb sufficient impact energy, particularly when applied to truck frames. A possible characteristic is required.
- Non-patent Document 1 and Patent Documents 1 and 2 disclose the technology of a steel plate excellent in impact energy absorption characteristics.
- these steel sheets have a structure containing retained austenite or martensite, and have achieved excellent impact characteristics by optimizing the metal structure of the steel sheet.
- the steel sheet having such a structure has a problem that the yield stress is low and there is a problem in bending formability.
- Patent Document 3 discloses a method of stably producing a thin steel plate having a high impact energy absorption capacity at a high yield by performing cold rolling.
- this method is disadvantageous in terms of manufacturing cost in addition to the fact that the heat affected zone (HAZ) of the arc weld zone is greatly softened and a sufficient weld joint strength cannot be obtained.
- HAZ heat affected zone
- Patent Document 8 As a technique for suppressing the softening of the weld heat affected zone, it is possible to strengthen precipitation by containing Ti by adding Mo and Nb or Ti to Patent Document 7 and optimizing the components in Patent Document 8. A method for suppressing the HAZ softening of steel is disclosed. However, these methods have a problem in that the material may be brittle fractured at a low temperature or the impact energy absorption amount may be reduced.
- Patent Document 9 manufactures hot-rolled steel sheets for high-strength ERW steel pipes with excellent low-temperature toughness and weldability by optimizing rolling conditions from rough rolling to finish rolling of steel slabs and subsequent cooling treatment.
- a method is disclosed. This method has a fine-grained metal structure by controlling recrystallization in rough rolling and finish rolling of steel slabs to obtain a steel sheet with excellent low-temperature toughness, but it controls the size and distribution of alloy carbonitrides. It is not intended. As a result, since these have not been optimized, there has been a problem that the impact energy absorption characteristics are lowered.
- Patent Document 10 discloses a method for producing a hot-rolled high-tensile steel sheet having excellent toughness and hydrogen-induced cracking resistance by optimizing the rolling reduction and holding time and finish rolling conditions in the rough rolling process of the steel slab. It is disclosed.
- the purpose of optimization of the rough rolling process in this method is to promote recrystallization of steel, but it is not intended to control the size and distribution of alloy precipitates. As a result, since these have not been optimized, there has been a problem that the impact energy absorption characteristics are lowered.
- the method described in Patent Document 10 has a problem that the size and distribution of alloy precipitates cannot be controlled, and good impact absorption energy cannot be obtained.
- Patent Document 11 discloses a technique for obtaining a high-strength hot-rolled steel sheet having excellent HAZ softening resistance characteristics by appropriately dispersing precipitated particles in a weld heat-affected zone.
- this technique disperses fine precipitates in the HAZ part of the steel plate during arc welding, but the size of the precipitate particles in the steel has not been optimized, resulting in impact energy absorption characteristics of the steel plate. There was a problem that was not good.
- the present invention has been made in view of the above problems, and its purpose is to provide a high yield specific hot rolled steel sheet having a maximum tensile strength of 600 MPa or more, which is excellent in both impact energy absorption characteristics at low temperature and HAZ softening resistance, and its production. It is to provide a method.
- the present inventors investigated in detail the influencing factors of the HAZ softening and low-temperature impact energy absorption characteristics of steel sheets containing alloy carbonitrides such as Ti that can stably obtain a high yield ratio. As a result, it was found that the HAZ softening amount can be suppressed by making the Ti amount, the Nb amount, and the Mn amount appropriate.
- the inventors then intensively studied a method for improving impact energy absorption characteristics at low temperatures, reducing the area fraction of pearlite as a metal structure of the steel sheet, and conventionally considered to be advantageous for improving impact energy absorption capacity.
- the precipitates are controlled so that they exist in a lattice-matched state having a specific crystal orientation relationship with the parent phase Fe.
- the alloy carbonitride in a precipitated state having good lattice matching with the parent phase Fe is unlikely to be an obstacle to crack initiation and propagation, while the parent phase Fe and It has been found that alloy carbonitrides that are in an inconsistent state reduce impact energy absorption at low temperatures even if their size is relatively small.
- the inventors have achieved both HAZ softening resistance and low-temperature energy absorption characteristics, a high yield ratio, and good bendability. Hot rolled steel sheets and plated steel sheets having a maximum tensile strength of 600 MPa or more were completed. That is, the gist of the present invention is as follows.
- the balance has a component composition consisting of Fe and inevitable impurities, The area fraction of pearlite is 5% or less, the total area fraction of martensite and retained austenite is 0.5% or less, and the balance consists of a metal structure that is one or two of ferrite and bainite, The average crystal grain size of ferrite and bainite is 10 ⁇ m or less, The average particle size of the alloy carbonitride that has been misaligned and contains Ti and Nb is 20 nm or less, Yield ratio is 0.85 or more, A high-yield specific hot-rolled steel sheet excellent in low-temperature impact
- the composition further contains one or more of Ca, Mg, La, and Ce in a mass% of 0.0003 to 0.01% in total.
- a steel slab comprising the composition according to any one of (1) to (5) above is heated to 1150 ° C. or higher, the heated steel slab is roughly rolled, and the temperature is between 1000 and 1080 ° C.
- the maximum rolling interval in the rough rolling performed at 1150 ° C. or less is 45 seconds or less, and after the rough rolling is finished, the holding time t1 (second) satisfying the following formula (1) is taken.
- finish rolling is started, finish rolling at the final rolling temperature Tf satisfying the following formula (2) is performed, and water cooling of the steel slab is started within 3 seconds after the finish rolling, and subsequently at a minimum cooling rate of 8 ° C / second or more.
- a method for producing a high-yield specific hot-rolled steel sheet excellent in low-temperature impact energy absorption characteristics and HAZ softening characteristics characterized by cooling a steel slab to 700 ° C. or lower and winding it in a range of 530 to 650 ° C. 1000 ⁇ ([% Ti] + [% Nb])> t1 Formula (1) Tf> 830 + 400 ([% Ti] + [% Nb]) Equation (2)
- the hot-rolled steel sheet of the present invention a high yield ratio hot-rolled steel sheet having a maximum tensile strength of 600 MPa or more and excellent in HAZ softening characteristics, low-temperature energy absorption characteristics, and excellent bending workability can be obtained with the above configuration.
- the hot rolled steel plate of the present invention can be used in a cold region. At the same time, it is possible to reduce the thickness of the parts by increasing the strength, and it can be expected to reduce the weight of construction equipment, automobiles or trucks.
- the maximum tensile strength is 600 MPa or more, the HAZ softening characteristics and impact energy absorption characteristics at low temperatures, Makes it possible to produce a high yield ratio hot rolled steel sheet excellent in bending workability.
- excellent absorption of impact energy at low temperature means that the impact energy absorption at ⁇ 40 ° C. is 70 J / cm 2 or more in the Charpy impact test.
- excellent bendability means that in a 90 ° V bending test, r lim / t is 1.0 or less, where t is the thickness of the specimen and r lim is the limit bending radius at which no cracks occur.
- C 0.04-0.09% If the C content is less than 0.04%, it is difficult to ensure a maximum tensile strength of 600 MPa or more. On the other hand, if it exceeds 0.09%, the alloy carbonitride containing Ti and Nb which is coarse and incoherently precipitated increases, and the impact energy absorption characteristics at low temperature are lowered, so that 0.04% to 0.09 % Restricted.
- Si: 0.4% or less If the Si content exceeds 0.4%, martensite or retained austenite may remain in the steel sheet structure, and the low temperature toughness and impact energy absorption characteristics will deteriorate. For this reason, the appropriate range was made 0.4% or less. From the viewpoint of securing the bending formability, it is more desirable to be 0.2% or less.
- the lower limit of the amount of Si is not particularly limited, but if it is less than 0.001%, the manufacturing cost increases, so 0.001% is the practical lower limit.
- Mn is an element that is used to secure the strength of the base metal through the control of the metal structure of the steel, and further contributes to the suppression of HAZ softening of the weld. If it is less than 1.2%, the area fraction of pearlite will increase, impact energy absorption characteristics at low temperatures will decrease, and the HAZ softening will increase, so the weld joint strength will greatly decrease with respect to the base metal strength. To do. If the content exceeds 2.0%, hard martensite may be formed, and the impact energy absorption characteristics at low temperatures are lowered. Therefore, the appropriate range is 2.0% or less. From the viewpoint of ensuring bend formability, it is more desirable to be 1.8% or less.
- P 0.1% or less P is used for securing the strength of the steel. However, if the content exceeds 0.1%, the low temperature toughness is lowered and the impact energy absorption characteristics at low temperatures cannot be obtained, so the appropriate range is made 0.1% or less.
- the lower limit is not particularly limited, but if it is less than 0.001%, the production cost increases, so 0.001% is the substantial lower limit.
- S 0.02% or less
- S is an element that affects impact energy absorption characteristics. If the content exceeds 0.02%, even if the area fraction of the metal structure and the average particle diameter of the alloy carbonitride are controlled, the impact energy absorption characteristics at low temperatures cannot be obtained. 02% or less.
- the lower limit is not particularly limited, but if it is less than 0.0003%, the production cost increases, so 0.0003% is a substantial lower limit.
- Al: 1.0% or less Al is used for deoxidation and control of the metal structure of the steel sheet. If it exceeds 1.0%, the heat-affected zone of arc welding becomes soft and sufficient weld joint strength cannot be obtained, so the appropriate range is made 1.0% or less.
- the lower limit is not particularly limited, but if it is less than 0.001%, the production cost increases, so 0.001% is the substantial lower limit.
- Nb 0.02 to 0.09%
- Nb is used as a precipitation strengthening element for adjusting the strength of steel and is used for suppressing softening of the welded HAZ. If it is less than 0.02%, the effect of suppressing the softening of the weld HAZ is not observed, and if it exceeds 0.09%, the alloy carbonitride containing Ti and Nb that is coarse and inconsistently precipitated increases. Since the impact energy absorption characteristics at low temperatures are lowered, the content is limited to the range of 0.02% to 0.09%.
- Ti 0.02 to 0.07%
- Ti is used as a precipitation strengthening element for adjusting the strength of the steel and is used for suppressing softening of the welded HAZ. If it is less than 0.02%, it is difficult to obtain a maximum tensile strength of 600 MPa or more. On the other hand, if it exceeds 0.07%, the alloy carbonitride containing Ti and Nb, which is coarse and inconsistently precipitated, increases and the impact energy absorption characteristics at low temperatures are lowered, so that 0.02% to 0.07%. % Restricted. In order to stably obtain a yield ratio of 0.85 or more, it is preferable to set 0.03% as the lower limit.
- N 0.005% or less
- N contributes to the crystal grain size of the metal structure of the steel sheet through the formation of nitrides. However, if it exceeds 0.005%, the alloy carbonitrides containing Ti and Nb which are coarse and inconsistently precipitated increase, and the impact energy absorption characteristics at low temperatures are lowered. Restricted to.
- the lower limit is not particularly limited, but if it is less than 0.0003%, the production cost increases, so 0.0003% is a substantial lower limit.
- Mn + 8 [% Ti] +12 [% Nb] is the sum of the contribution ratios of each element related to the impact energy absorption characteristics at low temperatures and the HAZ softening characteristics by welding. As shown in FIG. 1, when plotting the relationship between vE- 40 , which is an index of impact energy absorption characteristics, and ⁇ HV, which is an index of HAZ softening, for 11 steel types having different Ti and Nb, the value of this parameter is 2.
- HAZ softening resistance cannot be obtained (that is, ⁇ HV> 40), and it is difficult to obtain a maximum tensile strength of 600 MPa or more, and if it exceeds 2.6, coarse and inconsistent precipitation occurs.
- the alloy carbonitride containing Ti and Nb is increased, and the impact energy absorption characteristics at low temperature are lowered (ie, vE -40 ⁇ 70 J / cm 2 ). For this reason, the appropriate range is limited to the range of 2.0 to 2.6.
- the following elements may be selectively contained as steel components.
- V 0.01-0.12%
- V may be used for adjusting the strength of the steel. However, if the V content is less than 0.01%, the effect is not obtained, and if it exceeds 0.12%, embrittlement proceeds and the impact energy absorption characteristics at low temperatures are deteriorated. Therefore, the appropriate range is limited to 0.01 to 0.12%.
- B 0.0003 to 0.005%
- B may be used for the structure control of the steel sheet. However, if the amount of B is less than 0.0003%, the effect is not exhibited, and if it exceeds 0.005%, martensite may be formed, and impact energy absorption characteristics at low temperatures are deteriorated. . Therefore, the appropriate range is limited to 0.0003 to 0.005%.
- the steel components in this embodiment are not particularly limited with respect to other elements, and may appropriately contain various elements for adjusting the strength.
- the hot-rolled steel sheet of the present invention contains ferrite and bainite as the main phase, and the balance may include one or more of pearlite, martensite, and retained austenite.
- Perlite area fraction In the precipitation strengthened steel containing Nb and Ti, when the area fraction of pearlite exceeds 5%, brittle fracture is likely to occur at low temperature and the impact energy absorption characteristics are further reduced. Therefore, the upper limit is limited to 5%. From the viewpoint of securing bendability, 3% or less is a preferable range. The lower limit is not particularly defined, but the area fraction of pearlite is preferably closer to zero in terms of impact energy absorption characteristics.
- Total area fraction of martensite and retained austenite In the precipitation strengthened steel containing Nb and Ti, when the total area fraction of martensite and retained austenite exceeds 0.5%, brittle fracture is likely to occur at low temperatures, and impact energy absorption characteristics further deteriorate. For this reason, the upper limit of the total area fraction was limited to 0.5%. The lower limit is not particularly defined, but the total area fraction of martensite and retained austenite is more preferably close to zero in terms of impact energy absorption characteristics.
- the remaining metallographic structure is one or two ferrites and bainite. Although there is no restriction
- Average grain size of ferrite and bainite The average grain size of ferrite and bainite is a factor that correlates with embrittlement. If the average particle size exceeds 10 ⁇ m, even if the average particle size of the alloy carbonitride containing Nb and Ti is controlled, impact energy absorption characteristics at low temperatures may not be secured, so the upper limit is limited to 10 ⁇ m. did. 8 ⁇ m or less is a preferable condition that can secure the impact energy absorption characteristics more stably. Although a minimum is not specifically limited, Since manufacturing cost will increase significantly that it is less than 2 micrometers, 2 micrometers is a substantial minimum.
- the metal structure of the steel sheet can be observed with an optical microscope in accordance with JIS G 0551.
- the observation surface is etched with a nital etchant after the steel plate is polished.
- the area fraction of ferrite, bainite, pearlite, and martensite can be measured by a point count method or image analysis using a structure photograph taken with an optical microscope or a scanning electron microscope (SEM).
- the area fraction of retained austenite is measured by the X-ray diffraction method.
- bainite includes any of upper bainite, lower bainite, and granular bainite.
- the perlite includes perlite and pseudo perlite.
- crystal grain size can be measured by observation with an optical microscope or crystal orientation analysis by the EBSD method.
- crystal grain size is the average crystal grain size d described in JIS G 0551.
- Alage particle size of incoherently precipitated alloy carbonitride containing Ti and Nb The particle size of the alloy carbonitride containing Ti and Nb and the lattice matching between the matrix structure ferrite or bainite are important factors related to impact energy absorption characteristics at low temperatures. Generally, in precipitation-strengthened steels, it is known to precipitate fine alloy carbonitrides with good lattice matching with the matrix structure as fine particles, but in order to improve low temperature toughness and impact energy absorption characteristics Therefore, it is important to control alloy carbonitride particles having poor lattice matching with the matrix structure.
- the appropriate range is limited to 20 nm or less. From the viewpoint of obtaining more excellent impact energy absorption characteristics, 10 nm or less is a more preferable range. Although a minimum is not specifically limited, 2 nm is a substantial minimum as a size which can analyze the crystal orientation of a precipitate.
- the “non-aligned precipitated alloy carbonitride” is a state in which the matrix structure ferrite or bainite is not consistently precipitated, and the following crystal orientation relationship between adjacent ferrite or bainite This means one having no (Baker-Nutting orientation relationship).
- MX // (100) Fe (010) MX // (011) Fe (001) MX // (0-11) Fe (Note: -1 is shown as a substitute for a symbol with a bar on 1) where M represents Ti and Nb, and the occupation ratio of Ti and Nb Does not matter. X represents C and N, and the occupation ratio of C and N is not limited.
- V or Mo may be included in M.
- the crystal orientation analysis and average particle diameter measurement of the alloy carbonitride which has been inconsistently precipitated are performed using a transmission electron microscope (TEM).
- TEM transmission electron microscope
- the steel slab sample is thinned to such an extent that the electron beam is transmitted, and the crystal orientation analysis between the precipitate and the surrounding parent phase Fe is performed by TEM, and then, among the precipitates determined to be inconsistent precipitates Twenty average particle diameters are measured in order from the larger diameter.
- the particle diameter of the precipitate is measured as an equivalent circular diameter assuming a circle equivalent to the particle cross-sectional area.
- yield ratio is 0.85 or more If the yield ratio is less than 0.85, impact energy absorption characteristics at low temperatures may be deteriorated, and bending workability is also deteriorated. For this reason, the lower limit of the yield ratio was limited to 0.85.
- r lim / t is used as an evaluation standard for bending workability.
- t is the plate thickness of the test piece
- r lim is the limit bending radius at which cracking does not occur in the 90 ° V bending test
- r lim / t is 1.0 or less, which is excellent in bending workability.
- 0.5 or less is a more preferable range.
- the upper limit is not particularly limited, but if it exceeds 1.1, bending workability may be lowered, so 1.1 or less is a more preferable range.
- Maximum tensile strength 600 MPa or more If the maximum tensile strength is less than 600 MPa, there is no contribution to reducing the weight of members of automobiles, trucks, construction machines, etc., so in the present invention, a steel sheet having a maximum tensile strength of 600 MPa or more is assumed.
- the heating temperature of the steel slab was limited to 1150 ° C. or higher.
- the upper limit is not particularly defined, but if the temperature exceeds 1300 ° C., the effect is saturated, so this is a substantial upper limit.
- the heated steel slab is roughly rolled into a rough bar. This rough rolling needs to be completed between 1000 ° C. and 1080 ° C.
- finish temperature is less than 1000 ° C.
- coarse alloy carbonitride precipitates in austenite, and impact energy absorption characteristics at low temperatures are deteriorated.
- 1080 ° C. or more austenite crystal grains become coarse, finish rolling, cooling
- an average crystal grain size of 10 ⁇ m or less of ferrite and bainite cannot be obtained, and low-temperature toughness deteriorates and impact energy absorption characteristics deteriorate.
- the holding time between each reduction pass is an important parameter that affects the average particle diameter of inconsistent alloy carbonitrides.
- rough rolling is usually performed about 3 to 10 times, more preferably 5 to 10 times, but the maximum holding time t0 between each rolling performed at 1150 ° C. or less is 45 seconds or more.
- the alloy carbonitride becomes coarse enough to affect the impact energy absorption characteristics. For this reason, the holding time between each reduction pass was limited to 45 seconds or less. More preferably, it is within 30 seconds.
- the rough bar is finish-rolled to obtain a rolled material.
- the time (t1) from the end of rough rolling to the start of finish rolling is an important parameter that affects the average particle diameter of alloy carbonitride and the crystal grain sizes of ferrite and bainite after transformation.
- the retention time t1 (arrow in the figure) at which the impact energy absorption characteristic (vE- 40 ) changes from good (OK) to bad (NG) increases.
- the holding time t1 (seconds) for transitioning from good (OK) to bad (NG) substantially corresponds to 1000 ⁇ ([% Ti] + [% Nb]).
- the holding time t1 (second) from the end of rough rolling to the start of finish rolling is 1000 ⁇ ([% Ti] + [% Nb]) seconds or more, a coarse alloy carbonitride in austenite is formed. Precipitation, austenite crystal grains become coarse, average grain size of ferrite and bainite below 10 ⁇ m cannot be obtained in the post-transformation structure after finish rolling, cooling and winding, low temperature toughness deteriorates and impact energy Absorption characteristics decrease. 700 ⁇ ([% Ti] + [% Nb])> t1 seconds is a more preferable range. Therefore, the holding time t1 (second) is defined by the following formula (1). 1000 ⁇ ([% Ti] + [% Nb])> t1 Formula (1)
- the final rolling temperature Tf affects the average particle diameter of the alloy carbonitride and the crystal grain diameter of the ferrite and bainite after the transformation, and is therefore an important condition in the present invention.
- Ti and Nb It varies depending on the content.
- the final rolling temperature Tf is 830 + 400 ⁇ ([% Ti] + [% Nb]) or less, a coarse alloy carbonitride having no lattice matching to the parent phase is precipitated, and impact energy absorption characteristics at low temperatures are reduced.
- the final rolling temperature Tf is set so as to satisfy the following formula (2).
- Formula (2) This relational expression (2) is obtained from the relationship between the steel types shown in Table 2 and the final rolling temperature Tf shown later.
- FIG. 3 shows the relationship between Tf (° C.) and the mass% of Ti + Nb of the inventive examples and the comparative example 2 types (A-7, B-6) among the steel types shown in Table 2.
- the upper limit of the final rolling temperature Tf is not particularly limited, but the crystal grain size of ferrite and bainite tends to be coarse, and is preferably 970 ° C. or lower.
- Water cooling of the rolled material is performed immediately after the final rolling.
- the time from the end of the final rolling to the start of air cooling affects the base material toughness and impact energy absorption characteristics at low temperatures through the particle size of ⁇ and the average particle size of the alloy carbonitride. If the air cooling time immediately after the final rolling exceeds 3 seconds, the impact energy absorption characteristics tend to be reduced, so that water cooling is started within 3 seconds.
- the lower limit is not particularly defined, it is substantially 0.2 seconds or more in general equipment.
- the rolled material is cooled to a hot-rolled steel sheet.
- This cooling is an important process for controlling the metallographic structure. Cooling to 700 ° C. or lower at a minimum cooling rate of 8 ° C./second or higher.
- alloy carbonitrides When the cooling stop temperature exceeds 700 ° C., alloy carbonitrides are likely to precipitate coarsely on the grain boundaries, pearlite is easily formed, the ferrite crystal grain size is increased, and impact energy at low temperatures is increased. Absorption characteristics decrease. On the other hand, even when the minimum cooling rate to 700 ° C. is less than 8 ° C./second, alloy carbonitrides are likely to coarsely precipitate on the grain boundaries, pearlite is easily formed, and the ferrite grain size is further increased. Becomes larger, and impact energy absorption characteristics at low temperatures are deteriorated.
- the minimum cooling rate of 8 ° C./second or more means that the cooling rate between the temperature from the air cooling end temperature to 700 ° C. is not always lower than 8 ° C./second. For this reason, for example, it means that air cooling is not performed within this temperature section. Thus, in the present invention, air cooling is not performed in the middle of the cooling process by water cooling as in the prior art.
- the cooling stop temperature is more preferably 680 ° C. or less, and the minimum cooling rate is more preferably 15 ° C./second or more.
- the upper limit of the minimum cooling rate is not particularly defined, when it exceeds 80 ° C./second, it becomes difficult to cool uniformly in the hot-rolled coil, and the strength fluctuation in the coil becomes large. For this reason, it is preferable that it is 80 degrees C / sec or less.
- the winding temperature is 530 to 650 ° C.
- the coiling temperature is less than 530 ° C.
- martensite or retained austenite may be formed, and the toughness at low temperatures and the impact energy absorption characteristics are significantly reduced.
- the temperature exceeds 650 ° C. the area fraction of pearlite increases, and the toughness drop at low temperatures and the impact energy absorption characteristic drop become remarkable.
- the hot-rolled steel sheet thus obtained may be reheated (annealed).
- the reheating temperature exceeds the Ac3 temperature, coarse alloy carbonitrides are precipitated, and impact energy absorption characteristics at low temperatures are deteriorated.
- the suitable range of reheating temperature is restrict
- the heating method is not particularly specified, and may be performed by methods such as furnace heating, induction heating, current heating, and high frequency heating.
- the heating time is not particularly defined, but when the heating and holding time of 550 ° C. or higher exceeds 30 minutes, the maximum heating temperature is desirably 700 ° C. or lower in order to obtain a tensile strength of 590 MPa or higher.
- reheating may be performed after the hot-rolled steel sheet is wound and before the temperature reaches room temperature.
- skin pass rolling or leveler rolling is effective in improving shape correction, aging, and fatigue properties, it may be performed after pickling or before pickling.
- the upper limit of the rolling reduction be 3%. This is because if it exceeds 3%, the formability of the steel sheet is impaired. Moreover, you may perform pickling according to the objective.
- the hot dip galvanized steel sheet of the present invention is a steel sheet in which a plated layer or an alloyed plated layer is provided on the surface of the above-described hot rolled steel sheet of the present invention.
- the steel sheet After pickling the hot-rolled steel sheet obtained by the above-described method, the steel sheet is heated using a continuous galvanizing facility or a continuous annealing galvanizing facility, hot-plated, and a plated layer is formed on the surface of the hot-rolled steel plate. .
- the heating temperature of the steel plate exceeds the Ac3 temperature, the tensile strength of the steel plate is lowered and the impact energy absorption characteristics are lowered at a low temperature. Therefore, the appropriate range of the heating temperature is limited to the Ac3 temperature or lower. As the heating temperature is closer to Ac3, the tensile strength is drastically decreased and the material variation increases. Therefore, Ac3-30 ° C. or lower is a more preferable heating temperature range.
- galvanizing alloying treatment may be performed to form an alloyed galvanized layer.
- plating type is not limited to zinc plating, and other plating types may be used as long as the upper limit of the heating temperature is the Ac3 temperature.
- the production method preceding hot rolling is not particularly limited. That is, following the smelting by a blast furnace, a converter, an electric furnace, etc., component adjustment is performed so that the desired component content is obtained by various secondary scouring. Then, it may be cast by a method such as thin continuous slab casting in addition to normal continuous casting and casting by ingot method. Scrap may be used as a raw material. In the case of a slab obtained by continuous casting, it may be sent directly to a hot rolling mill as it is at a high temperature slab, or may be hot rolled after being cooled to room temperature and then reheated in a heating furnace.
- Steels A to AC having chemical components shown in Table 1 were produced by the following method. First, a steel slab was produced by casting, and then the steel slab was reheated and roughly rolled under the hot rolling conditions and annealing plating conditions shown in Table 2-1 and Table 2-2 to form a rough bar. Next, the rough bar was finish-rolled to form a rolled material having a thickness of 4 mm, and then cooled and wound up as a hot-rolled steel plate.
- the chemical composition of the steel in Table 1 is the steel no. Steel No. in Table 2 with the same alphabet. It corresponds to the chemical composition of steel.
- SRT in Table 2 indicates the slab heating temperature (° C.).
- RFT indicates the rough rolling end temperature (° C.).
- T0 indicates the maximum holding time (seconds) between each rough rolling performed at 1150 ° C. or less.
- T1 indicates the time (seconds) from the end of rough rolling to the start of finish rolling.
- Tf indicates the final finish rolling temperature (° C.).
- T2 indicates the air cooling time (seconds) immediately after the final finish rolling.
- CRmin indicates the minimum cooling rate (° C./second) between SCT after air cooling.
- SCT indicates a water cooling stop temperature (° C.).
- CT indicates a coiling temperature (° C.).
- Steels A-12 to 14 and C-2 are hot-dip galvanized steel sheets, which are pickled hot-rolled steel sheets, then annealed at the annealing temperatures shown in Table 2 in a continuous annealing galvanizing line, and then galvanized. Made to go.
- the galvanization immersion temperature was set to 450 ° C.
- the galvanized alloying treatment was performed at an alloying temperature of 500 ° C.
- the observation of the metal structure of the steel sheet was performed with an optical microscope for the L cross section in accordance with JIS G 0551.
- the area fraction of each structure is calculated using the point count method or image analysis in the region of 1 / 4t thickness of L section (position of 1 / 4t from the steel plate surface when the plate thickness is t) using the structure photograph. Measured by.
- the value of the nominal grain size was calculated based on JISG0552.
- the crystal orientation analysis and average particle diameter measurement of alloy carbonitrides with inconsistent precipitation containing Ti and Nb were made by thinning the steel slab sample to the extent that the electron beam was transmitted, and using a transmission electron microscope (TEM). And by observing 20 or more alloy carbonitrides.
- TEM transmission electron microscope
- a lap joint was produced by arc welding.
- the welding atmosphere was CO 2 : 100%, and the heat input was in the range of about 5000 to 8000 J / cm.
- the cross section is polished, the Vickers hardness test of the base material and the weld heat affected zone (HAZ) is performed, and it indicates that it is 0 or less.
- Table 3 “F” is ferrite, “B” is bainite, “A” is retained austenite, “M” is martensite, “P” is pearlite, and “d (F, B) ” is ferrite.
- HAZ And bainite average grain size ( ⁇ m)
- d MCN is the average grain size (nm) of alloy carbonitride that has been misaligned
- ⁇ HV the Vickers hardness of the softest part of the weld heat affected zone. HAZ , where the Vickers hardness of the material is HV BM , it represents the difference between HV BM and HV HAZ .
- the strength characteristics of the steel sheet were evaluated by the following method. First, the specimen was processed into a No. 5 test piece described in JIS Z 2201. And the tensile test was done with respect to this No. 5 test piece according to the method of JISZ2241, and the maximum tensile strength (TS), yield strength (YS), and elongation (EI) were calculated
- TS maximum tensile strength
- YS yield strength
- EI elongation
- the impact energy absorption characteristics at low temperatures were evaluated by the Charpy impact test. Based on JIS2202, a 2 mm V notch test piece having a plate thickness of 3 mm was prepared, and after the test piece was cooled to ⁇ 40 ° C., a Charpy impact test was performed, and the impact energy absorption value (J / cm 2 ) was measured.
- the bending test was performed by the JISZ224 V-block method (bending angle: 90 °), and the thickness of the test piece was measured as t, and the limit bending radius r lim at which no crack was generated was measured.
- Steel A-2 is a comparative example in which the tensile strength was less than 600 MPa and the impact energy absorption characteristics at low temperatures were low because the slab heating temperature was outside the proper range.
- Steels A-3 to 4 and Steels B-3 to 4 are comparative examples in which the impact energy absorption characteristics at low temperatures were low because the rough rolling end temperature was outside the proper range.
- Steel A-6 and Steel B-3 are comparative examples having low impact energy absorption characteristics at low temperatures because the time from the end of rough rolling to the start of finish rolling was outside the proper range.
- Steel A-11 and Steel B-10 are comparative examples having low impact energy absorption characteristics at low temperatures because the water cooling stop temperature after finish rolling and the coiling temperature of the hot-rolled steel sheet are outside the proper ranges.
- Steel A-12 and Steel B-11 are comparative examples in which the tensile strength is less than 600 MPa and the impact energy absorption characteristics at low temperatures are low because the coiling temperature of the hot rolled steel sheet is outside the proper range.
- Steel A-15 is a comparative example having low impact energy absorption characteristics at low temperatures because the annealing temperature was higher than the Ac3 temperature.
- Steels F-1, Q-1, S-1, AB-1, and AC-1 are comparative examples in which the HAZ softening amount was large because the values of Mn amount, Ti amount, and Nb amount were outside the proper ranges. .
- Steels F-1, Q-1, and AC-1 have a tensile strength of less than 600 MPa.
- Steel G-1 is a comparative example in which the strength is less than 600 MPa and the HAZ softening amount is large because the C amount is outside the proper range.
- Steels H-1, I-1, K-1, and AB-1 have martensite or retained austenite because the C, Si, and Mn contents are outside the proper ranges, and impact energy absorption characteristics at low temperatures This is a comparative example having a low bend and poor bendability.
- Steel J-1 is a comparative example in which pearlite was present and the impact energy absorption characteristics at low temperatures were low because the amount of Mn was outside the proper range.
- Steels M-1 and O-1 are comparative examples having low impact energy absorption characteristics at low temperatures because of excessive amounts of S and P.
- Steel P-1 is a comparative example in which HAZ was softened because the amount of Al was excessive.
- all of the examples of the present invention had a yield ratio of 0.85 or more, a maximum tensile strength of 600 MPa or more, and excellent characteristics in impact energy absorption characteristics and HAZ softening resistance at low temperatures. .
Abstract
Description
即ち、本発明の要旨は以下の通りである。
C:0.04~0.09%、
Si:0.4%以下、
Mn:1.2~2.0%、
P:0.1%以下、
S:0.02%以下、
Al:1.0%以下、
Nb:0.02~0.09%、
Ti:0.02~0.07%
N:0.005%以下
を含有し、
2.0≦Mn+8[%Ti]+12[%Nb]≦2.6であり、
残部がFeおよび不可避的不純物からなる成分組成を有し、
パーライトの面積分率が5%以下、マルテンサイトおよび残留オーステナイトの合計面積分率が0.5%以下、残部がフェライトおよびベイナイトの1種または2種である金属組織からなり、
フェライトおよびベイナイトの平均結晶粒径が10μm以下であり、
TiおよびNbを含有する非整合析出した合金炭窒化物の平均粒子径が20nm以下であり、
降伏比が0.85以上、
最大引張強度が600MPa以上である
ことを特徴とする低温での衝撃エネルギー吸収特性と耐HAZ軟化特性に優れた高降伏比熱延鋼板。
1000×([%Ti]+[%Nb])>t1 ・・・・・ 式(1)
Tf>830+400([%Ti]+[%Nb]) ・・ 式(2)
Tf>830+800([%Ti]+[%Nb]) ・・ 式(3)
まず、本発明の低温での衝撃エネルギー吸収特性と耐HAZ軟化特性に優れた高降伏比熱延鋼板の鋼成分を限定した理由について説明する。ここで、成分についての「%」は質量%を意味する。
C量が0.04%未満であると、最大引張強度600MPa以上を確保することが困難である。一方、0.09%を超えると粗大でかつ非整合析出したTiおよびNbを含有する合金炭窒化物が増加し、低温での衝撃エネルギー吸収特性が低くなるので、0.04%~0.09%の範囲内に制限した。
Si量が0.4%を超えると、マルテンサイトあるいは残留オーステナイトが鋼板組織内に残存する場合があり、低温での靭性および衝撃エネルギー吸収特性が低下する。このため、その適正範囲を0.4%以下とした。曲げ成形性確保の観点から、0.2%以下であることがより望ましい。Si量の下限は特に限定しないが、0.001%未満であると製造コストが増大するため、0.001%が実質的な下限である。
Mnは鋼の金属組織制御を通じて母材の強度確保のために用いられ、さらに溶接部のHAZ軟化抑制に寄与する元素である。1.2%未満であると、パーライトの面積分率が増加して低温での衝撃エネルギー吸収特性が低下し、さらにHAZ軟化量が大きくなるため、溶接継ぎ手強度が母材強度に対して大きく低下する。2.0%を超えて含有すると、硬質なマルテンサイトが形成される場合が有り、低温での衝撃エネルギー吸収特性が低下することから、その適正範囲は2.0%以下とする。曲げ成形性を確保する観点からは1.8%以下であることがより望ましい。
Pは鋼の強度確保のために用いられる。しかしながら、0.1%を超えて含有すると、低温靭性が低下し、さらに低温での衝撃エネルギー吸収特性を得られないため、その適正範囲を0.1%以下とする。下限は特に限定しないが、0.001%未満であると製造コストが増大するため、0.001%が実質的な下限である。
Sは衝撃エネルギー吸収特性に影響する元素である。0.02%を超えて含有すると、金属組織の面積分率と合金炭窒化物の平均粒子径を制御しても、低温での衝撃エネルギー吸収特性を得られないため、その適正範囲を0.02%以下とする。下限は特に限定しないが、0.0003%未満であると製造コストが増大するため、0.0003%が実質的な下限である。
Alは脱酸および鋼板の金属組織制御のために用いられる。1.0%を超えるとアーク溶接の熱影響部が軟質化し、十分な溶接継ぎ手強度が得られないので、その適正範囲を1.0%以下とする。下限は特に限定しないが、0.001%未満であると製造コストが増大するため、0.001%が実質的な下限である。
Nbは析出強化元素として鋼の強度調整に用いられると共に、溶接HAZの軟化を抑制するために用いられる。0.02%未満であると、溶接HAZの軟化抑制効果が観られず、また0.09%を超えると、粗大でかつ非整合析出したTiおよびNbを含有する合金炭窒化物が増加し、低温での衝撃エネルギー吸収特性が低くなるので、0.02%~0.09%の範囲内に制限した。
Tiは析出強化元素として鋼の強度調整に用いられると共に、溶接HAZの軟化を抑制するために用いられる。0.02%未満であると、最大引張強度:600MPa以上を得ることが困難である。また0.07%を超えると、粗大でかつ非整合析出したTiおよびNbを含有する合金炭窒化物が増加し、低温での衝撃エネルギー吸収特性が低くなるので、0.02%~0.07%の範囲内に制限した。降伏比で0.85以上を安定的に得るために、0.03%を下限とすることが好ましい。
Nは窒化物の形成を通じて鋼板の金属組織の結晶粒径に寄与する。しかしながら、0.005%を超えると粗大でかつ非整合析出したTiおよびNbを含有する合金炭窒化物が増加し、低温での衝撃エネルギー吸収特性が低くなるので、0.005%以下の範囲内に制限した。
下限は特に限定しないが、0.0003%未満であると製造コストが増大するため、0.0003%が実質的な下限である。
「Mn+8[%Ti]+12[%Nb]」は、低温での衝撃エネルギー吸収特性と溶接によるHAZ軟化特性に関連する各元素の寄与割合の合計である。図1に示すように、Ti、Nbが異なる11鋼種について衝撃エネルギー吸収特性の指標であるvE-40と、HAZ軟化量の指標であるΔHVとの関係をプロットすると、本パラメータの値が2.0未満であると、十分な耐HAZ軟化特性が得られない(即ち、ΔHV>40)と共に、最大引張強度600MPa以上を得ることが難しくなり、2.6を超えると粗大でかつ非整合析出したTiおよびNbを含有する合金炭窒化物が増加し、低温での衝撃エネルギー吸収特性が低くなる(即ち、vE-40<70J/cm2)。このため、その適正範囲を2.0~2.6の範囲に制限した。
Vは鋼の強度調整のために用いてもよい。しかしながら、Vの含有量が0.01%未満であると、その効果がなく、また、0.12%を超えると脆化が進み、低温での衝撃エネルギー吸収特性が低下する。このため、その適正範囲を0.01~0.12%に限定した。
Cr、Cu、Ni、Moは、鋼の組織制御のために用いてもよい。しかしながら、これらの元素の1種又は2種以上の合計含有量が0.02%未満であると、添加に伴う上記効果が無く、また、2.0%を超えるとオーステナイトが残留し、低温での衝撃エネルギー吸収特性が低下する。このため、これら元素の合計量の適正範囲を0.02~2.0%に限定した。
Bは鋼板の組織制御に用いてもよい。しかしながら、B量が0.0003%未満であると、その効果は発現せず、また、0.005%を超えると、マルテンサイトが形成することがあり、低温での衝撃エネルギー吸収特性が低下する。このため、その適正範囲を0.0003~0.005%に制限した。
Ca、Mg、La、Ceは、鋼の脱酸のために用いてもよい。しかしながら、これらの元素の1種又は2種以上の合計量が0.0003%未満であると、その効果は無く、また、0.01%を超えると低温で脆性破壊し、衝撃エネルギー吸収特性が低下する。このため、その適正範囲を0.0003~0.01%に制限した。
Nb及びTiを含有する析出強化鋼において、パーライトの面積分率が5%を超えると、低温で脆性破壊しやすくなり、更に衝撃エネルギー吸収特性が低下するため、その上限を5%に制限した。曲げ性確保の観点から、3%以下が好ましい範囲である。なお、下限は特に定めないが、パーライトの面積分率はゼロに近い方が衝撃エネルギー吸収特性に関してより好ましい。
Nb及びTiを含有する析出強化鋼において、マルテンサイトと残留オーステナイトの合計面積分率が0.5%を超えると、低温で脆性破壊しやすくなり、更に衝撃エネルギー吸収特性が低下する。このため、合計面積分率の上限を0.5%に制限した。なお、下限は特に定めないが、マルテンサイトと残留オーステナイトの合計面積分率はゼロに近い方が衝撃エネルギー吸収特性に関してより好ましい。
それぞれの面積分率は特に制限は無いが、曲げ加工性を確保する観点から、ベイナイト面積分率を10%以上含むことが好ましい。
フェライトとベイナイトの平均結晶粒径は脆化と相関関係のある因子である。平均粒径が10μmを超えると、NbとTiを含有する合金炭窒化物の平均粒子径を制御しても、低温での衝撃エネルギー吸収特性を確保できない場合があるため、その上限を10μmに制限した。8μm以下がより安定的に衝撃エネルギー吸収特性を確保できる好ましい条件である。下限は特に限定しないが、2μm未満であると製造コストが大幅に増加するので、2μmが実質的な下限である。
TiおよびNbを含有する合金炭窒化物の粒径と母相組織であるフェライトまたはベイナイトとの格子整合性は、低温での衝撃エネルギー吸収特性と関係する重要な因子である。一般的に、析出強化鋼においては、母相組織と格子整合性の良い微細合金炭窒化物を微細粒子として析出させることが知られているが、低温靭性改善と衝撃エネルギー吸収特性改善のためには、母相組織と格子整合性の悪い合金炭窒化物粒子の制御が重要である。格子整合性を悪くする非整合析出した合金炭窒化物の平均粒子径が20nmを超えると、低温での衝撃エネルギー吸収特性が低下するため、その適正範囲を20nm以下に限定した。より優れた衝撃エネルギー吸収特性を得る観点から、10nm以下がより好ましい範囲である。下限は特に限定しないが、析出物の結晶方位の解析が可能なサイズとして、2nmが実質的な下限である。
(100)MX // (100)Fe
(010)MX // (011)Fe
(001)MX // (0-11)Fe (注:-1は1の上にバーが付いた記号の代わりとして表す)ここで、MはTi、Nbを示し、Ti、Nbの占有分率は問わない。またXはC、Nを示し、C、Nの占有分率は問わない。VやMoを添加した場合には、Mの中にVやMoが含まれる場合がある。
降伏比が0.85未満であると、低温での衝撃エネルギー吸収特性が低下する場合が有り、また曲げ加工性も低下する。このため、降伏比の下限を0.85に制限した。
最大引張強度が600MPa未満であると、自動車、トラック、建設機械等の部材軽量化に寄与がないことから、本発明においては最大引張強度:600MPa以上の鋼板を前提とした。
1000×([%Ti]+[%Nb])>t1 ・・・・・ 式(1)
Tf>830+400([%Ti]+[%Nb]) ・・・ 式(2)
この関係式(2)は、後に示す表2の鋼種と最終圧延温度Tfとの関係から求められる。図3は、表2に示す鋼種のうち本発明例及び比較例2種(A-7、B-6)のTi+Nbの質量%とTf(℃)との関係を表している。ここで、「a([%Ti]+[%Nb])」部分の係数aを400とした場合、即ち、式(2)が、-40℃での衝撃吸収エネルギーvE-40が70J/cm2以上となる境界であることが分かる。
Tf>830+800([%Ti]+[%Nb]) ・・・ 式(3)
の場合は、係数aが400の場合よりも、-40℃での衝撃吸収エネルギーvE-40が70J/cm2以上となる境界から少し離れる。しかし、係数aが、400~800の領域では、仕上げ圧延開始までの待ち時間が長くなり、合金炭窒化物が析出し始める可能性が高くなるので、係数aが800の式(3)に基づいて、Tfをコントロールすることが好ましい。
Ac3=910-210√[%C]+45[%Si]-30[%Mn]+700[%P]+40[%Al]+400[%Ti]+32[%Mo]-11[%Cr]-20[%Cu]-15[%Ni]
式中、%C、%Si、%Mn、%P、%Al、%Ti、%Mo、%Cr、%Cu、%Niは、それぞれC、Si、Mn、P、Al、Ti、Mo、Cr、Cu及びNiの鋼中の含有量を示す。
鋼J-1は、Mn量が適正範囲外のため、パーライトが存在し、低温での衝撃エネルギー吸収特性が低かった比較例である。
Claims (10)
- 質量%で、
C:0.04~0.09%、
Si:0.4%以下、
Mn:1.2~2.0%、
P:0.1%以下、
S:0.02%以下、
Al:1.0%以下、
Nb:0.02~0.09%、
Ti:0.02~0.07%、
N:0.005%以下
を含有し、
2.0≦Mn+8[%Ti]+12[%Nb]≦2.6であり、
残部がFeおよび不可避的不純物からなる成分組成を有し、
パーライトの面積分率が5%以下、マルテンサイトおよび残留オーステナイトの合計面積分率が0.5%以下、残部がフェライトおよびベイナイトの1種または2種である金属組織からなり、
フェライトおよびベイナイトの平均結晶粒径が10μm以下であり、
TiおよびNbを含有する非整合析出した合金炭窒化物の平均粒子径が20nm以下であり、
降伏比が0.85以上、
最大引張強度が600MPa以上である
ことを特徴とする低温での衝撃エネルギー吸収特性と耐HAZ軟化特性に優れた高降伏比熱延鋼板。 - さらに、質量%で、V:0.01~0.12%を含有することを特徴とする請求項1に記載の低温での衝撃エネルギー吸収特性と耐HAZ軟化特性に優れた高降伏比熱延鋼板。
- さらに、質量%で、Cr、Cu、Ni、Moの1種又は2種以上を合計で0.02~2.0%含有することを特徴とする請求項1または2に記載の低温での衝撃エネルギー吸収特性と耐HAZ軟化特性に優れた高降伏比熱延鋼板。
- さらに、質量%で、Bを0.0003~0.005%含有することを特徴とする請求項1~3の何れか1項に記載の低温での衝撃エネルギー吸収特性と耐HAZ軟化特性に優れた高降伏比熱延鋼板。
- さらに、質量%で、Ca、Mg、La、Ceの1種又は2種以上を合計で0.0003~0.01%含有することを特徴とする請求項1~4の何れか1項に記載の低温での衝撃エネルギー吸収特性と耐HAZ軟化特性に優れた高降伏比熱延鋼板。
- 請求項1~5の何れか1項に記載の高降伏比熱延鋼板の表面にめっきあるいは合金化めっきが施されていることを特徴とする低温での衝撃エネルギー吸収特性と耐HAZ軟化特性に優れた高降伏比熱延めっき鋼板。
- 請求項1~5の何れか1項に記載の成分組成からなる鋼片を、
1150℃以上に加熱し、
加熱された鋼片を粗圧延し、1000~1080℃間で粗圧延を終了し、この際、1150℃以下で行う粗圧延における最大の圧延間隔が45秒以下であり、
粗圧延終了後、下記式(1)を満たす保持時間t1(秒)をとった後、仕上げ圧延を開始し、
下記式(2)を満たす最終圧延温度Tfである仕上げ圧延を行い、
仕上げ圧延後3秒以内に鋼片の水冷を開始し、引き続き最低冷却速度8℃/秒以上で700℃以下まで鋼片を冷却して、530~650℃の範囲内で巻き取る
ことを特徴とする低温での衝撃エネルギー吸収特性と耐HAZ軟化特性に優れた高降伏比熱延鋼板の製造方法。
1000×([%Ti]+[%Nb])>t1 ・・・・・ 式(1)
Tf>830+400([%Ti]+[%Nb]) ・・ 式(2) - 最終圧延温度Tfが、下記式(3)を満たすことを特徴とする請求項7記載の高降伏比熱延鋼板の製造方法。
Tf>830+800([%Ti]+[%Nb]) ・・ 式(3) - 請求項7又は8に記載の製造方法で得られた熱延鋼板を酸洗の後、Ac3温度以下で加熱を行い、次いでめっき浴中に浸漬させて、該鋼板表面をめっきすることを特徴とする低温での衝撃エネルギー吸収特性と耐HAZ軟化特性に優れた高降伏比熱延めっき鋼板の製造方法。
- 前記めっき後に、さらにめっき合金化処理を行うことを特徴とする請求項9に記載の低温での衝撃エネルギー吸収特性と耐HAZ軟化特性に優れた高降伏比熱延めっき鋼板の製造方法。
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RU2014108831/02A RU2562582C1 (ru) | 2011-08-09 | 2012-08-08 | Горячекатаный стальной лист с высоким отношением предела текучести к пределу прочности, который имеет превосходные характеристики поглощения энергии удара при низкой температуре и устойчивость к размягчению зоны термического влияния (haz), и способ его получения |
JP2013502930A JP5354130B2 (ja) | 2011-08-09 | 2012-08-08 | 低温での衝撃エネルギー吸収特性と耐haz軟化特性に優れた高降伏比熱延鋼板およびその製造方法 |
CN201280038678.8A CN103732776B (zh) | 2011-08-09 | 2012-08-08 | 在低温下的冲击能吸收特性和耐haz软化特性优异的高屈服比热轧钢板及其制造方法 |
BR112014002875-3A BR112014002875B1 (pt) | 2011-08-09 | 2012-08-08 | chapas de aço laminadas a quente, e métodos para produção das mesmas |
EP12822363.3A EP2743364B1 (en) | 2011-08-09 | 2012-08-08 | Hot-rolled steel sheet having high yield ratio and excellent low-temperature impact energy absorption and haz softening resistance and method for producing same |
MX2014001501A MX349893B (es) | 2011-08-09 | 2012-08-08 | Lamina de acero laminada en caliente de alta proporcion de rendimiento, que tiene excelente absorcion de energia de impacto a baja temperatura y resistencia al reblandecimiento de la haz y metodo de produccion de la misma. |
US14/236,371 US20140178712A1 (en) | 2011-08-09 | 2012-08-08 | High yield ratio hot rolled steel sheet which has excellent low temperature impact energy absorption and haz softening resistance and method of production of same |
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KR101518551B1 (ko) | 2013-05-06 | 2015-05-07 | 주식회사 포스코 | 충격특성이 우수한 초고강도 열연강판 및 그 제조방법 |
KR101543837B1 (ko) | 2013-07-11 | 2015-08-11 | 주식회사 포스코 | 내충격 특성이 우수한 고항복비 고강도 열연강판 및 그 제조방법 |
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JP2017512905A (ja) * | 2014-03-25 | 2017-05-25 | ティッセンクルップ スチール ヨーロッパ アクチェンゲゼルシャフトThyssenKrupp Steel Europe AG | 高強度の平鋼製品を製造するための方法 |
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CN103732776A (zh) | 2014-04-16 |
BR112014002875A2 (pt) | 2017-02-21 |
MX349893B (es) | 2017-08-18 |
EP2743364A1 (en) | 2014-06-18 |
CN105648311A (zh) | 2016-06-08 |
KR20140026574A (ko) | 2014-03-05 |
CA2843588A1 (en) | 2013-02-14 |
TW201313920A (zh) | 2013-04-01 |
JPWO2013022043A1 (ja) | 2015-03-05 |
ES2589640T3 (es) | 2016-11-15 |
MX2014001501A (es) | 2014-05-12 |
BR112014002875B1 (pt) | 2018-10-23 |
US20140178712A1 (en) | 2014-06-26 |
RU2562582C1 (ru) | 2015-09-10 |
ZA201400954B (en) | 2016-07-27 |
PL2743364T3 (pl) | 2017-01-31 |
EP2743364B1 (en) | 2016-07-27 |
TWI453287B (zh) | 2014-09-21 |
EP2743364A4 (en) | 2015-11-04 |
CN103732776B (zh) | 2016-06-08 |
JP5354130B2 (ja) | 2013-11-27 |
CA2843588C (en) | 2018-02-20 |
KR101575832B1 (ko) | 2015-12-08 |
CN105648311B (zh) | 2018-03-30 |
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