WO2013051231A1 - 溶接熱影響部の低温靭性に優れた高張力鋼板およびその製造方法 - Google Patents
溶接熱影響部の低温靭性に優れた高張力鋼板およびその製造方法 Download PDFInfo
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- WO2013051231A1 WO2013051231A1 PCT/JP2012/006269 JP2012006269W WO2013051231A1 WO 2013051231 A1 WO2013051231 A1 WO 2013051231A1 JP 2012006269 W JP2012006269 W JP 2012006269W WO 2013051231 A1 WO2013051231 A1 WO 2013051231A1
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
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- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
Definitions
- the present invention relates to a high-strength steel plate used for steel structures such as ships, offshore structures, pressure vessels, and penstock, and a method for producing the same.
- the yield strength Yield Point
- the yield strength is 620 MPa or more, which not only excels in the strength and toughness of the base metal, but also low-temperature toughness of multi-pass welded zone with low to medium heat input welding.
- the present invention relates to a high-tensile steel plate excellent in (low-temperature toughness)) and a method for producing the same.
- Steel used for ships, marine structures, and pressure vessels is welded and finished as a structure with a desired shape. Therefore, these steels have high base metal strength and excellent toughness from the viewpoint of structural safety, and also have excellent toughness in welded joints (welded metal and heat-affected zone). It is required to be.
- CTOD test Crack Opening Displacement Test
- the local embrittlement zone is a weld heat affected zone (HAZ: Heat Affected Zone) that is subject to a complex thermal history due to multi-layer welding such as thick steel, and it is likely to occur, and the bond zone (between weld metal and base metal) And the part where the bond part is reheated to the two-phase region (the region that becomes coarse in the first cycle welding and is heated to the two-phase region of ferrite and austenite by the subsequent welding pass, hereinafter the two-phase region reheated part) Becomes the local embrittlement zone.
- HZ Heat Affected Zone
- the bond part Since the bond part is exposed to a high temperature just below the melting point, the austenite grains become coarse and are easily transformed into an upper bainite structure having low toughness by subsequent cooling, so that the matrix itself has low toughness. Further, in the bond portion, brittle structures such as Woodmannstatten structure and island martensite (Martensite-Austenite Constituent) are easily generated, and the toughness is further reduced.
- Patent Document 1 and Patent Document 2 disclose a technique for suppressing the austenite grain growth and improving weld toughness by adding rare earth elements (REM) together with Ti and dispersing fine particles in the steel. Is disclosed.
- REM rare earth elements
- Patent Document 3 in the case of a CTOD test, an embrittled portion caused by precipitation hardening due to V, which is a precipitation-type element in multilayer welding, becomes a local embrittlement region and lowers the critical CTOD value.
- a type high strength steel is proposed.
- Patent Document 4 discloses a technique for mainly increasing the addition amount of Mn to 2% or more.
- the composition of the component is made high Mn, and the amount of oxygen is controlled to an appropriate amount, thereby increasing the number of intragranular transformed ferrite nuclei and refining the microstructure of the weld heat affected zone, and C, Nb, V It is described that the value of a parameter equation composed of embrittlement elements such as the above is controlled to improve the CTOD characteristics (CTOD toughness) of HAZ.
- alloy elements such as Mn are easily segregated at the center of the slab, and the center segregation increases not only in the base metal but also in the heat-affected zone of the weld and becomes the starting point of fracture. Causes toughness to decrease.
- Patent Document 6 proposes that after continuous casting, the slab in the middle of solidification is reduced by the surface to produce a slab without central segregation, and the structure in the vicinity of the weld bond is improved by the composite oxide. .
- Patent Document 7 for a minute region including segregation at the central portion of the plate thickness at the in-plate position corresponding to the central portion of the slab, an average analysis value of the component is obtained, and a segregation parameter equation is derived to design the component. is suggesting.
- Patent Documents 8 and 9 disclose a technique for securing the base metal strength by adding low Cu and low Si, suppressing the formation of island martensite and improving toughness, and adding Cu. These increase the strength by precipitation of Cu by aging treatment, but since a large amount of Cu is added, hot ductility is lowered and productivity is hindered.
- Patent Document 10 control of the slab heating temperature of continuous cast steel pieces to reduce center segregation, the amount of B mixed in the steel composition, and island martensite
- control of the slab heating temperature of continuous cast steel pieces to reduce center segregation, the amount of B mixed in the steel composition, and island martensite We are proposing steel materials that can obtain excellent CTOD characteristics in multilayer welds with low to medium heat input by comprehensive measures such as component composition that suppresses the generation of slag.
- Patent Document 11 discloses that the effective crystal grain size, which is a fracture unit of HAZ coarse grains in the case of high heat input welding, is reduced, and in the case of welding with small to medium heat input, island martensite is reduced and grains due to a small amount of Nb. It is described that the CTOD characteristics of multi-layer welds can be improved in a welding heat input range of up to 100 kJ / cm by making the component composition capable of improving the field hardenability, suppressing precipitation hardening, and reducing the HAZ hardness. ing.
- the present invention has a yield strength suitable for steel structures such as ships, offshore structures, pressure vessels, penstocks, and the like, and has a CTOD characteristic of the weld heat affected zone of multilayer welds by small to medium heat input.
- An object of the present invention is to provide a high-tensile steel plate that is excellent in resistance and a method for producing the same.
- the inventors have ensured the base metal strength and toughness with a yield strength of 620 MPa or more, improved the toughness of the weld heat affected zone of multilayer welding, and have a CTOD characteristic with a test temperature of ⁇ 10 ° C. and a critical CTOD value of 0.50 mm or more.
- the present invention was made by further study based on the obtained knowledge, 1.
- C 0.05 to 0.14%
- Si 0.01 to 0.30% or less
- Mn 0.3 to 2.3%
- P 0.008% or less
- S 0.00. 005% or less
- Al 0.005 to 0.1%
- Ni 0.5 to 4%
- B 0.0003 to 0.003%
- N 0.001 to 0.008%
- Ceq [C] + [Mn] / 6 + [Cu + Ni] / 15 + [Cr + Mo + V] / 5
- each element symbol is content (mass%)) ⁇ 0.80
- the central segregation part hardness index (HCS) is (1 ) Satisfying the formula, the balance being a component composition consisting of Fe and inevitable impurities, and the hardness of the central segregation part of the steel sheet satisfying the formula (2) High tensile steel plate.
- [M] is the content of each element (mass%) HV max / HV ave ⁇ 1.35 + 0.006 / C ⁇ t / 750
- HV max is the maximum value of the Vickers hardness of the center segregation part
- HV ave is the average value of the Vickers hardness of the center segregation part and the front and back surfaces excluding 1/4 of the plate thickness
- C is the carbon content (% by mass)
- T is the plate thickness (mm) of the steel plate. 2.
- the low temperature of the heat affected zone according to 1 or 2 wherein the steel composition further contains, by mass%, Ti: 0.005 to 0.025% and Ca: 0.0005 to 0.003%.
- the sheet thickness center temperature is cooled to 350 ° C. or lower at a cooling rate of 0.3 ° C./s or higher.
- a method for producing a high-tensile steel sheet having excellent low-temperature toughness in the weld heat affected zone characterized by performing tempering at 450 ° C. to 680 ° C.
- a high-strength steel sheet having a yield strength of 620 MPa or more suitable for use in large steel structures such as offshore structures and excellent in low-temperature toughness, especially CTOD characteristics, of multi-layer welds with small to medium heat input, and its A manufacturing method is obtained and is extremely useful in industry.
- the component composition and the thickness direction hardness distribution are defined. 1.
- % is mass%.
- C 0.05 to 0.14% C is an element necessary for ensuring the strength of the base material as a high-tensile steel plate. If it is less than 0.05%, the hardenability deteriorates, and in order to secure the strength, it is necessary to add a large amount of a hardenability improving element such as Cu, Ni, Cr, Mo, etc., resulting in high costs and poor weldability. Invite. On the other hand, addition exceeding 0.14% leads to a significant decrease in weldability and a decrease in weld zone toughness. Therefore, the C content is in the range of 0.05 to 0.14%. Preferably, it is 0.07 to 0.13%.
- Si 0.01 to 0.30% Si is a component added as a deoxidizing element and for obtaining the strength of the base material. However, since a large amount of addition exceeding 0.30% causes a decrease in weldability and a decrease in weld joint toughness, the Si amount needs to be 0.01 to 0.30%. Preferably, it is 0.25% or less.
- Mn 0.3 to 2.3% Mn is added in an amount of 0.3% or more to ensure the base metal strength and weld joint strength. However, addition over 2.3% lowers the weldability, leads to excessive hardenability, and lowers the base metal toughness and weld joint toughness, so the range is 0.3 to 2.3%.
- P 0.008% or less
- P is an impurity which is inevitably mixed, and lowers the base metal toughness and weld zone toughness, and particularly when the content exceeds 0.008% in the weld zone, the toughness is significantly reduced. 0.008% or less.
- S 0.005% or less
- S is an impurity that is inevitably mixed, and if contained in excess of 0.005%, the toughness of the base metal and the welded portion is lowered, so the content is made 0.005% or less. Preferably, it is 0.0035% or less.
- Al 0.005 to 0.1%
- Al is an element added to deoxidize molten steel and needs to be contained in an amount of 0.005% or more.
- the base metal and welded portion toughness are reduced, and it is mixed into the welded metal portion by dilution by welding to reduce the toughness, so it is limited to 0.1% or less. Preferably, it is 0.08% or less.
- Ni 0.5-4% Ni improves the strength and toughness of the steel and is effective in improving the low temperature toughness of the welded portion, so 0.5% or more is added. On the other hand, at the same time as being an expensive element, excessive addition reduces hot ductility, so that the surface of the slab is likely to be scratched during casting, so the upper limit is made 4%.
- B 0.0003 to 0.003% B segregates at the austenite grain boundaries and suppresses the ferrite transformation from the grain boundaries, thereby improving the hardenability of the steel by adding a small amount.
- the effect is obtained by adding 0.0003% or more. However, if it exceeds 0.003%, it precipitates as carbonitride and the like, and the hardenability is lowered and the toughness is lowered. Therefore, the content is made 0.0003 to 0.003%. Preferably, it is 0.0005 to 0.002%.
- N 0.001 to 0.008% N reacts with Al to form precipitates, thereby refining crystal grains and improving base material toughness. Moreover, it is an element required in order to form TiN which suppresses the coarsening of the structure
- HCS 5.5 [C] 4/3 +15 [P] +0.90 [Mn] +0.12 [Ni] +0.53 [Mo] ⁇ 2.5, where [M] is the content of each element ( % By mass) and 0 for elements not contained.
- This parameter formula is a central segregation part hardness index composed of components that are easily concentrated in the central segregation part, and is obtained experimentally. If the value of this parameter formula exceeds 2.5, the CTOD characteristics deteriorate, so it is set to 2.5 or less. Preferably it is 2.3 or less. Since the CTOD test is a full-thickness steel plate test, it becomes a toughness evaluation with specimens including center segregation. When the concentration of components due to center segregation is remarkable, a hardened zone is generated in the weld heat affected zone, which is a good value. Cannot be obtained.
- the above is the basic component composition of the present invention, but when further improving the characteristics, Cr: 0.2 to 2.5%, Mo: 0.1 to 0.7%, V: 0.005 to 0.1 %, Cu: 0.49% or less, Ti: 0.005 to 0.025%, Ca: 0.0005 to 0.003%, or one or more selected from them.
- Cr 0.2 to 2.5% Cr is an element effective for increasing the strength of the base material by addition of 0.2% or more. However, if added in a large amount, the toughness is adversely affected, so when added, the content is made 0.2 to 2.5%.
- Mo 0.1 to 0.7% Mo is an element effective for increasing the strength of the base material by addition of 0.1% or more. However, if added in a large amount, the toughness is adversely affected, so when added, it is 0.1 to 0.7%, preferably 0.1 to 0.6%.
- V 0.005 to 0.1%
- V is an element effective for improving the strength and toughness of the base material when added in an amount of 0.005% or more. However, if it exceeds 0.1%, the toughness is reduced, so when added, 0.005 to 0.1% is added.
- Cu 0.49% or less Cu is an element having an effect of improving the strength of steel. However, if it exceeds 0.49%, it causes hot brittleness and deteriorates the surface properties of the steel sheet.
- Ti 0.005 to 0.025%
- Ti precipitates as TiN when the molten steel solidifies, suppresses coarsening of austenite in the welded portion, and contributes to improved toughness of the welded portion.
- the addition is less than 0.005%, the effect is small.
- TiN becomes coarse, and the effect of improving the toughness of the base metal and the welded part cannot be obtained. 0.005 to 0.025%.
- Ca 0.0005 to 0.003%
- Ca is an element that improves toughness by fixing S. In order to obtain this effect, addition of at least 0.0005% is necessary. However, even if the content exceeds 0.003%, the effect is saturated. Therefore, when it is added, it is added in the range of 0.0005 to 0.003%.
- HV max / HV ave ⁇ 1.35 + 0.006 / Ct / 750, where C is the carbon content (mass%), t is the plate thickness (mm)
- HV max / HV ave is a dimensionless parameter representing the hardness of the central segregation part, and if the value becomes higher than the value obtained by 1.35 + 0.006 / Ct / 750, the CTOD value decreases, so 1.35 + 0. 006 / Ct / 750 or less.
- HV max is the hardness of the center segregation part, and the range of (plate thickness / 10) mm including the center segregation part in the thickness direction is measured at intervals of 0.25 mm with a Vickers hardness tester (load 10 kgf). The maximum value among the measured values.
- HV ave is an average value of hardness.
- the range excluding the center segregation part from (surface thickness / 4) mm from the surface layer to (surface thickness / 4) from the surface layer is the load of 10 kgf of the Vickers hardness tester.
- the steel of the present invention is preferably produced by the production method described below.
- Molten steel adjusted to the component composition within the scope of the present invention is melted by a usual method using a converter, electric furnace, vacuum melting furnace or the like. Subsequently, after making it a slab through the process of continuous casting, it is made into desired plate
- the slab heating temperature and the rolling ratio (rolling reduction ratio slab thickness / plate thickness) during hot rolling are the mechanical properties of the steel sheet. The effect on characteristics is small. However, in a thick material, when the slab heating temperature is too low or the amount of reduction is insufficient, initial defects at the time of steel ingot production remain in the center of the plate thickness, and the quality of the steel plate is significantly reduced. Therefore, the slab heating temperature is set to 1050 ° C. or more and the reduction ratio is set to 2 or more so that casting defects existing in the slab are steadily pressed by hot rolling.
- the upper limit of the slab heating temperature does not need to be set in particular, but excessively high temperature heating may cause precipitates such as TiN deposited during solidification to become coarse, resulting in a decrease in the toughness of the base metal and the welded part, It is preferable that the heating temperature is 1200 ° C. or less from the viewpoint of generating a thick scale and causing surface defects during rolling, and from the viewpoint of energy saving.
- Cooling after hot rolling When the cooling rate is 0.3 ° C./s or more and less than 0.3 ° C./s to 350 ° C. or less, sufficient strength of the base material cannot be obtained. Further, if the cooling is stopped at a temperature higher than 350 ° C., the ⁇ ⁇ ⁇ transformation is not completely completed, so that a high-temperature transformation structure is formed, and high strength and high toughness are not compatible.
- the cooling rate is a value at the thickness center of the steel plate.
- the temperature at the center of the plate thickness is obtained by simulation calculation or the like from the plate thickness, surface temperature, cooling conditions, and the like. For example, the plate thickness center temperature is obtained by calculating the temperature distribution in the plate thickness direction using the difference method.
- the reheating temperature after hot rolling is 880 ° C. or higher and the reheating temperature is lower than 880 ° C., since the austenitization is insufficient, the strength and toughness do not satisfy the targets, the reheating temperature is 880 ° C. or higher, preferably Set to 900 ° C or higher.
- the upper limit temperature of the reheating temperature is not particularly defined, but heating to an excessively high temperature is preferably 1000 ° C. or less because austenite grains become coarse and cause toughness reduction.
- Tempering temperature 450 ° C to 680 ° C If the tempering temperature is less than 450 ° C., sufficient tempering effect cannot be obtained. On the other hand, tempering at a tempering temperature exceeding 680 ° C. is not preferable because carbonitride precipitates coarsely and toughness decreases. Further, tempering is preferably carried out by induction heating, because the coarsening of carbides during tempering is suppressed. In that case, the temperature at the center of the thickness of the steel sheet calculated by a simulation such as a difference method is set to 450 ° C. to 680 ° C.
- a tensile test was conducted by taking a JIS No. 4 test piece so that the longitudinal direction of the test piece was perpendicular to the rolling direction of the steel plate from 1/2 part of the thickness of the steel plate, yield strength and tensile strength. (Tensile Strength) was measured.
- a JIS V notch test piece was taken from 1/2 part of the thickness of the steel sheet so that the longitudinal direction of the test piece was perpendicular to the rolling direction of the steel sheet, and the absorbed energy at ⁇ 40 ° C. (vE ⁇ 40 ° C.).
- a material satisfying all of YP ⁇ 620 MPa, TS ⁇ 720 MPa, and vE ⁇ 40 ° C. ⁇ 100 J was evaluated as having good base material characteristics.
- a multi-layer welded joint was produced by submerged arc welding with a welding heat input of 45 to 50 kJ / cm using a K-shaped groove.
- the absorbed energy at a temperature of ⁇ 40 ° C. was measured with the weld bond part on the straight side of the 1/4 part of the steel sheet as the notch position in the Charpy impact test.
- the average of the three pieces satisfying vE ⁇ 40 ° C. ⁇ 100 J was judged to have good weld joint toughness.
- the CTOD value at ⁇ 10 ° C. was measured with the straight-side weld bond part as the notch position of the three-point bending CTOD test piece, and the minimum CTOD value of the test quantity of 3 was 0.50 mm or more. Was good.
- Steels A to E and N are invention examples, and steels F to M are comparative examples that do not satisfy the constituent ranges of the claims.
- Examples 1, 2, 5, 6, 10, 11, and 20 satisfy the components and production conditions of the present invention, and good base material characteristics and CTOD characteristics are obtained. Further, vE-40 ° C. ⁇ 100 J is satisfied.
- Example 3 was an example of air cooling after reheating, and the cooling rate was less than 0.3 ° C./s, so the target base material strength was not obtained.
- Example 4 has a cooling stop temperature exceeding 350 ° C
- Example 8 has a heating temperature of less than 880 ° C
- Example 9 has a tempering temperature of less than 450 ° C. The strength and toughness are not obtained.
- Example 7 since the reduction ratio is less than 2, the target base material toughness and the CTOD value at the welded portion are not obtained.
- Example 12 since the C addition amount is outside the lower limit range of the present invention, the target base material toughness is not obtained. Further, in Example 14, the amount of Ni added was outside the lower limit range of the present invention, so the CTOD value at the target weld was not obtained.
- Example 18 since the B addition amount is outside the lower limit range of the present invention, the strength and toughness of the target base material are not obtained.
- Example 3 Example 4, Example 8, Example 9, Example 12, and Example 18 in which the target base material strength and toughness were not obtained, the CTOD test and Charpy test of the welded part were Not implemented.
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Abstract
Description
1.質量%で、C:0.05~0.14%、Si:0.01~0.30%以下、Mn:0.3~2.3%、P:0.008%以下、S:0.005%以下、Al:0.005~0.1%、Ni:0.5~4%、B:0.0003~0.003%、N:0.001~0.008%を含有し、Ceq(=[C]+[Mn]/6+[Cu+Ni]/15+[Cr+Mo+V]/5、各元素記号は含有量(質量%))≦0.80、中心偏析部硬さ指標(HCS)が(1)式を満たし、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、鋼板の中心偏析部の硬さが(2)式を満足することを特徴とする溶接熱影響部の低温靭性に優れた高張力鋼板。
HCS(=5.5[C]4/3+15[P]+0.90[Mn]+0.12[Ni]+0.53[Mo]) ≦2.5 ・・・(1)
ここで、[M]は各元素の含有量(質量%)
HVmax/HVave≦1.35+0.006/C-t/750 ・・・(2)
HVmaxは中心偏析部のビッカース硬さの最大値、HVaveは中心偏析部と表裏面から板厚の1/4を除く部分のビッカース硬さの平均値、Cは炭素の含有量(質量%)、tは鋼板の板厚(mm)。
2.鋼組成に、更に、質量%で、Cr:0.2~2.5%、Mo:0.1~0.7%、V:0.005~0.1%、Cu:0.49%以下の中から選ばれる1種または2種以上を含有することを特徴とする、1に記載の溶接熱影響部の低温靭性に優れた高張力鋼板。
3.鋼組成に、更に、質量%で、Ti:0.005~0.025%、Ca:0.0005~0.003%を含有することを特徴とする1または2記載の溶接熱影響部の低温靭性に優れた高張力鋼板。
4.1ないし3のいずれか一つに記載の成分組成を有する鋼を1050℃以上に加熱後、圧下比(元厚/最終厚)が2以上となるように熱間圧延を施す。880℃以上の温度に再加熱後、0.3℃/s以上の冷速で板厚中心温度が350℃以下まで冷却する。その後、450℃~680℃に焼戻し処理を施すことを特徴とする溶接熱影響部の低温靭性に優れた高張力鋼板の製造方法。
1.成分組成
成分組成の限定理由について説明する。説明において%は質量%とする。
C:0.05~0.14%
Cは、高張力鋼板としての母材強度確保に必要な元素である。0.05%未満では焼入性が低下し、強度確保のために、Cu、Ni、Cr、Moなどの焼入性向上元素の多量添加が必要となり、コスト高と、溶接性の低下とを招く。一方、0.14%を超える添加は溶接性を著しく低下させることに加え、溶接部靭性低下を招く。従って、C量は0.05~0.14%の範囲とする。好ましくは、0.07~0.13%である。
Siは、脱酸元素として、また、母材強度を得るために添加する成分である。しかし、0.30%を超える多量の添加は、溶接性の低下と溶接継手靭性の低下を招くので、Si量は0.01~0.30%とする必要がる。好ましくは、0.25%以下である。
Mnは母材強度および溶接継手強度を確保するため、0.3%以上添加する。しかし、2.3%を超える添加は、溶接性を低下させ、焼入性の過剰を招き、母材靭性および溶接継手靭性を低下させるため、0.3~2.3%の範囲とする。
Pは不可避的に混入する不純物で、母材靭性および溶接部靭性を低下させ、特に溶接部において含有量が0.008%を超えると靭性が著しく低下するので、0.008%以下とする。
Sは、不可避的に混入する不純物で、0.005%を超えて含有すると母材および溶接部靭性を低下させるため、0.005%以下とする。好ましくは、0.0035%以下である。
Alは、溶鋼を脱酸するために添加される元素であり、0.005%以上含有させる必要がある。一方、0.1%を超えて添加すると母材および溶接部靭性を低下させるとともに、溶接による希釈によって溶接金属部に混入し、靭性を低下させるので、0.1%以下に制限する。好ましくは、0.08%以下である。
Niは、鋼の強度と靭性を向上させ、溶接部の低温靭性の向上に有効なため0.5%以上を添加する。一方で、高価な元素であるのと同時に、過度の添加は熱間延性を低下させるために、鋳造時にスラブの表面にキズが発生しやすくなるので、上限を4%とする。
Bは、オーステナイト粒界に偏析し、粒界からのフェライト変態を抑制することにより、微量添加で鋼の焼入性を高める効果がある。その効果は、0.0003%以上の添加で得られる。しかし、0.003%を超えると炭窒化物などとして析出し、焼入性が低下し靭性が低下するため、0.0003~0.003%とする。好ましくは、0.0005~0.002%である。
Nは、Alと反応して析出物を形成することで、結晶粒を微細化し、母材靭性を向上させる。また、溶接部の組織の粗大化を抑制するTiNを形成させるために必要な元素であり、0.001%以上含有させる。一方、0.008%を超えて含有すると母材や溶接部の靭性を著しく低下させることから、上限を0.008%とする。
Ceqが0.80を超えると溶接性や溶接部靭性が低下するため、0.80以下とする。好ましくは、0.75以下である。但し、Ceq=[C]+[Mn]/6+[Cu+Ni]/15+[Cr+Mo+V]/5、各元素記号は含有量(質量%)とし、含有しない元素は0とする。
Crは、0.2%以上の添加で母材を高強度化するのに有効な元素である。しかし、多量に添加すると靭性に悪影響を与えるので、添加する場合は、0.2~2.5%とする。
Moは、0.1%以上の添加で母材を高強度化するのに有効な元素である。しかし、多量に添加すると靭性に悪影響を与えるので、添加する場合は0.1~0.7%、好ましくは0.1~0.6%である。
Vは、0.005%以上の添加で母材の強度と靭性の向上に有効な元素である。しかし、0.1%を超えると靭性低下を招くので、添加する場合は0.005~0.1%の添加とする。
Cuは、鋼の強度向上の効果を有する元素である。しかし、0.49%を超えると、熱間脆性を引き起こして鋼板の表面性状劣化させるため、添加する場合は0.49%以下とする。
Tiは、溶鋼が凝固する際にTiNとなって析出し、溶接部におけるオーステナイトの粗大化を抑制し、溶接部の靭性向上に寄与する。しかし、0.005%未満の添加ではその効果が小さく、一方、0.025%を超えて添加すると、TiNが粗大化し、母材や溶接部靭性改善効果が得られないため、添加する場合は、0.005~0.025%とする。
Caは、Sを固定することによって靭性を向上する元素である。この効果を得るためには、少なくとも0.0005%の添加が必要である。しかし、0.003%を超えて含有してもその効果は飽和するため、添加する場合は、0.0005~0.003%の範囲で添加する。
HVmax/HVave≦1.35+0.006/C-t/750,但しCは炭素の含有量(質量%)、tは板厚(mm)
HVmax/HVaveは中心偏析部の硬さを表す無次元パラメータで、その値が1.35+0.006/C-t/750で求まる値より高くなるとCTOD値が低下するため、1.35+0.006/C-t/750以下とする。
本発明範囲内の成分組成に調整した溶鋼を転炉、電気炉、真空溶解炉などを用いた通常の方法で溶製する。次いで、連続鋳造の工程を経てスラブとした後、熱間圧延により所望の板厚とし、その後冷却し、焼戻し処理を施す。
本発明の場合、熱間圧延時のスラブ加熱温度および圧下比(rolling reduction ratio = slab thickness / plate thickness)が鋼板の機械的特性に及ぼす影響は小さい。しかしながら、厚肉材において、スラブ加熱温度が低すぎる場合や、圧下量が不十分な場合、板厚中心部に鋼塊製造時の初期欠陥が残存し、鋼板の内質が著しく低下する。そのため、スラブに存在する鋳造欠陥を熱間圧延によって着実に圧着させるためスラブ加熱温度を1050℃以上、圧下比を2以上とする。
スラブ加熱温度の上限は特に定める必要は無いが、過度の高温加熱は凝固時に析出したTiNなどの析出物が粗大化し、母材や溶接部の靭性が低下することや、高温では鋼塊表面のスケールが厚く生成し、圧延時に表面疵の発生原因になること、省エネルギーの観点などから、加熱温度は、1200℃以下とするのが好ましい。
冷却速度が0.3℃/s未満では十分な母材の強度が得られない。また、350℃より高い温度で冷却を停止するとγ→α変態が完全に完了しないため、高温変態組織が生成し、高強度と高靭性が両立しない。冷却速度は鋼板の板厚中心での値とする。板厚中心での温度は、板厚、表面温度および冷却条件等から、シミュレーション計算等により求められる。例えば、差分法を用い、板厚方向の温度分布を計算することにより、板厚中心温度を求める。
再加熱温度が880℃より低い場合、オーステナイト化が不十分のために、強度と靭性が目標を満足しないため、再加熱温度は880℃以上、好ましくは900℃以上とする。再加熱温度の上限温度は特に規定しないが、過度に高温まで加熱することはオーステナイト粒が粗大化して靭性の低下を招くことになるため、好ましくは1000℃以下である。
450℃未満の焼戻し温度では十分な焼戻しの効果が得られない。一方、680℃を超える焼戻し温度で焼戻しを行うと、炭窒化物が粗大に析出し、靭性が低下するために好ましくない。また、焼戻しは誘導加熱により行うと焼戻し時の炭化物の粗大化が抑制されて好ましい。その場合は、差分法などのシミュレーションによって計算される鋼板の板厚中心での温度が450℃~680℃となるようにする。
Claims (5)
- 質量%で、C:0.05~0.14%、Si:0.01~0.30%以下、Mn:0.3~2.3%、P:0.008%以下、S:0.005%以下、Al:0.005~0.1%、Ni:0.5~4%、B:0.0003~0.003%、N:0.001~0.008%を含有し、Ceq(=[C]+[Mn]/6+[Cu+Ni]/15+[Cr+Mo+V]/5、各元素記号は含有量(質量%))≦0.80、中心偏析部硬さ指標HCSが(1)式を満たし、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、鋼板の中心偏析部の硬さが(2)式を満足することを特徴とする溶接熱影響部の低温靭性に優れた高張力鋼板。
HCS=5.5[C]4/3+15[P]+0.90[Mn]+0.12[Ni]+0.53[Mo] ≦2.5 ・・・(1)
ここで、[M]は各元素の含有量(質量%)
HVmax/HVave≦1.35+0.006/C-t/750 ・・・(2)
HVmaxは中心偏析部のビッカース硬さの最大値、HVaveは中心偏析部と表裏面から板厚の1/4を除く部分のビッカース硬さの平均値、Cは炭素の含有量(質量%)、tは鋼板の板厚(mm)。 - 鋼組成に、更に、質量%で、Cr:0.2~2.5%、Mo:0.1~0.7%、V:0.005~0.1%、Cu:0.49%以下の中から選ばれる1種または2種以上を含有することを特徴とする、請求項1に記載の溶接熱影響部の低温靭性に優れた高張力鋼板。
- 鋼組成に、更に、質量%で、Ti:0.005~0.025%、Ca:0.0005~0.003%を含有することを特徴とする請求項1または2記載の溶接熱影響部の低温靭性に優れた高張力鋼板。
- 請求項1または2のいずれか一つに記載の成分組成を有する鋼を1050℃以上に加熱後、圧下比が2以上となるように熱間圧延を施し、880℃以上の温度に再加熱後、0.3℃/s以上の冷速で板厚中心温度が350℃以下まで冷却し、その後、450℃~680℃に焼戻し処理を施すことを特徴とする溶接熱影響部の低温靭性に優れた高張力鋼板の製造方法。
- 請求項3に記載の成分組成を有する鋼を1050℃以上に加熱後、圧下比が2以上となるように熱間圧延を施し、880℃以上の温度に再加熱後、0.3℃/s以上の冷速で板厚中心温度が350℃以下まで冷却し、その後、450℃~680℃に焼戻し処理を施すことを特徴とする溶接熱影響部の低温靭性に優れた高張力鋼板の製造方法。
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JP2017078208A (ja) * | 2015-10-21 | 2017-04-27 | Jfeスチール株式会社 | 鋼材の製造方法および鋼材用熱処理設備 |
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WO2021255858A1 (ja) * | 2020-06-17 | 2021-12-23 | 日本製鉄株式会社 | 鋼板 |
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US10443110B2 (en) | 2014-03-20 | 2019-10-15 | Jfe Steel Corporation | High toughness and high tensile strength thick steel plate and production method therefor |
US10358688B2 (en) | 2014-04-24 | 2019-07-23 | Jfe Steel Corporation | Steel plate and method of producing same |
JP2017078208A (ja) * | 2015-10-21 | 2017-04-27 | Jfeスチール株式会社 | 鋼材の製造方法および鋼材用熱処理設備 |
WO2021255858A1 (ja) * | 2020-06-17 | 2021-12-23 | 日本製鉄株式会社 | 鋼板 |
JPWO2021255855A1 (ja) * | 2020-06-17 | 2021-12-23 | ||
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KR101608719B1 (ko) | 2016-04-04 |
JP5924058B2 (ja) | 2016-05-25 |
JPWO2013051231A1 (ja) | 2015-03-30 |
EP2765210A1 (en) | 2014-08-13 |
EP2765210A4 (en) | 2015-06-24 |
JP2013091845A (ja) | 2013-05-16 |
CN103874777A (zh) | 2014-06-18 |
JP5817832B2 (ja) | 2015-11-18 |
US9945015B2 (en) | 2018-04-17 |
CN103874777B (zh) | 2017-03-15 |
US20140246131A1 (en) | 2014-09-04 |
KR20140064933A (ko) | 2014-05-28 |
EP2765210B1 (en) | 2018-12-19 |
SG11201400459WA (en) | 2014-05-29 |
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