CN107208215B - 高强度电焊钢管、高强度电焊钢管用钢板的制造方法和高强度电焊钢管的制造方法 - Google Patents
高强度电焊钢管、高强度电焊钢管用钢板的制造方法和高强度电焊钢管的制造方法 Download PDFInfo
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- CN107208215B CN107208215B CN201680006469.3A CN201680006469A CN107208215B CN 107208215 B CN107208215 B CN 107208215B CN 201680006469 A CN201680006469 A CN 201680006469A CN 107208215 B CN107208215 B CN 107208215B
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Classifications
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- C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
- C21D9/505—Cooling thereof
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K11/00—Resistance welding; Severing by resistance heating
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- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K11/00—Resistance welding; Severing by resistance heating
- B23K11/16—Resistance welding; Severing by resistance heating taking account of the properties of the material to be welded
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- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B1/00—Layered products having a non-planar shape
- B32B1/08—Tubular products
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- B32B15/00—Layered products comprising a layer of metal
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Abstract
一种电焊钢管,能确保近年来对油井管所要求的高强度和高韧性。其成分组成以质量%计,在钢管的母材部,将下述点作为基准点的情况下,以所述基准点为中心在厚度方向的两侧具有0.5mm的宽度的区域中的金属组织由10面积%以下的多边形铁素体和余量的贝氏体铁素体构成,所述点是作为在厚度方向上距表面的距离为厚度的1/4的点而规定的点;厚度为15mm以上。
Description
技术领域
本发明涉及高强度电焊钢管,特别是涉及强度和韧性均以高水平兼备的高强度电焊钢管。另外,本发明涉及这样的钢管所使用的钢板的制造方法以及这样的钢管的制造方法。
背景技术
近年来,油井、气井的钻掘深度有愈来愈大的倾向,为了提高套管(casing)等的压溃强度,强烈要求油井管高强度化。最近,为了谋求钻掘成本的削减,对高强度、且不实施对造管后的钢管整体的热处理的、造管状态的电焊钢管的需求提高。
为了提高钢材的强度,充分地含有碳量是有效,曾提出了一种将碳含量设为0.25质量%以上,在造管状态下具有800MPa以上的抗拉强度的电焊钢管(参照专利文献1(日本特开平07-102321号公报))。但是,在含有大量的碳来提高了强度的情况下,有时钢材的韧性降低。
另外,为了提高钢材的强度,利用作为马氏体和贝氏体等的硬质金属组织的低温相变组织也是有效的。而且,在电焊钢管的制造工序中进行造管、定径(sizing)等,因此也可将由冷加工引起的加工硬化用于强度的提高。通过将这样的组织强化和加工硬化组合,提供在造管状态下抗拉强度为862MPa以上的电焊钢管(参照专利文献2(国际公开第2012/144248号))。
发明内容
在专利文献2的技术中,制造作为电焊钢管的坯料(母材)的热轧钢板时,降低卷取温度,使金属组织为贝氏体从而确保了强度,但这终究是通过使钢板的板厚以及径较小来实现的。与此相对,在制造板厚更大且板宽度也大的钢板的情况下,从制造性的观点出发,希望提高卷取温度,但若提高卷取温度,则难以均以高水平确保钢板的强度和韧性。
另外,在为了使韧性提高而降低钢板的碳量并确保了强度的情况下,添加有钛以及硼的低碳成分系(低C-Ti-B系)是有利的。但是,为了提高油井管的压溃强度,不仅要求高强度化还要求厚壁化。对于添加有钛以及硼的低碳成分系(低C-Ti-B系)的钢材,在谋求厚壁化的情况下,热轧制后的卷取温度变高,因此有可能钢板的强度以及韧性降低。
本发明人进行了专心研究,结果得到以下见解:在制造厚壁的油井管时,若使钢板的板厚较大,则即使是(低C-Ti-B系)的成分系,也不能够以高水平兼备强度和韧性。另外还得到以下见解:由板厚的增大导致的上述倾向特别是在板厚15mm以上的电焊钢管用热轧钢板中较显著。
本发明是鉴于上述情况而完成的,其目的是提供能够以高的水平兼备对油井管所要求的强度和韧性的高强度电焊钢管。
另外,本发明的目的还在于提供用于上述高强度电焊钢管的高强度电焊钢管用钢板的制造方法、以及上述高强度电焊钢管的制造方法。
本发明人专心研究了能够以高的水平兼备对油井管所要求的强度和韧性的高强度电焊钢管。其结果,本发明人得到以下见解:(I)将电焊钢管的制造所用的热轧钢板的成分系设为含有使淬硬性提高、而且也能得到析出强化的效果的元素Mo的(低C-Ni-Cu-Mo系),并且,(II)适当控制热轧结束后的热轧钢板的冷却速度以及卷取温度,可得到具有机械特性(强度和韧性)优异的金属组织的电焊钢管制造用的热轧钢板,(III)即使电焊钢管的厚度为规定值以上,也能得到强度和韧性优异的高强度电焊钢管。再者,还得到以下见解:(IV)如果在使用上述热轧钢板(母钢板)造管之后对焊接部(焊接区)实施适当的热处理,则在焊接部能够确保与钢管部同样的优异的强度以及韧性。
本发明是基于以上的见解而完成的,其要旨如下。
(1)一种高强度电焊钢管,其特征在于,
成分组成以质量%计含有
C:0.040~0.070%、
Si:0.10~0.50%、
Mn:1.60~2.00%、
Nb:0.020~0.080%、
V:0.060%以下、
Ti:0.010~0.025%、
Mo:0.20~0.40%、
Ni:0.10~0.50%、
Al:0.050%以下、
3Mo%+Ni%:超过1.00%,
余量包含Fe以及不可避免的杂质,
在钢管的母材部,将下述点作为基准点的情况下,以上述基准点为中心在厚度方向的两侧具有0.5mm的宽度的区域中的金属组织由10面积%以下的多边形铁素体和余量的贝氏体铁素体(Bainitic Ferrite)构成,所述点是作为在厚度方向上距表面的距离为厚度的1/4的点而规定的点,
厚度为15.0~19.8mm。
(2)根据上述(1)所述的高强度电焊钢管,
上述成分组成以质量%计还含有
P:0.030%以下、
S:0.004%以下、
N:0.006%以下、
O:0.004%以下。
(3)根据上述(1)或(2)所述的高强度电焊钢管,
上述成分组成以质量%计还含有
Cu:0.10~0.50%、
Cr:0.05~0.50%
Ca:0.0005~0.0040%
REM:0.0005~0.0050%
之中的一种或两种以上。
(4)根据上述(3)所述的高强度电焊钢管,
3Mo%+Ni%+Cu%超过1.20%。
(5)根据上述(1)~(4)的任一项所述的高强度电焊钢管,
上述多边形铁素体的平均粒径为20μm以下。
(6)根据上述(1)~(5)的任一项所述的高强度电焊钢管,
上述金属组织的机械特性是:轴向的抗拉强度超过725MPa;轴向的屈服强度为655~758MPa;在0℃下周向的夏比冲击吸收能为22J以上。
(7)一种高强度电焊钢管用钢板的制造方法,其特征在于,
将具有上述(1)~(3)的任一项中所述的成分组成的热轧钢板在790℃以上进行热轧,以8~15℃/秒的平均冷却速度冷却,在500~630℃进行卷取,并且,在相变开始时以超过5℃/秒的冷却速度冷却。
(8)根据上述(7)所述的高强度电焊钢管用钢板的制造方法,
上述相变开始时的温度低于665℃。
(9)根据上述(7)或(8)所述的高强度电焊钢管用钢板的制造方法,
上述热轧钢板是将铸坯加热并实施950℃以下的累计压下率为50%以上的热轧制而得到的热轧钢板。
(10)一种高强度电焊钢管的制造方法,其特征在于,
将采用上述(7)~(9)的任一项所述的方法制造的钢板成形为管状,对上述钢板的端部进行电阻焊接,并将焊接部的外表面加热到950~1050℃,在焊接部的内表面以8℃/秒以上的冷却速度冷却到上述外表面的冷却停止温度600~450℃。
再者,制造出这样电焊钢管后,可以适当进行定径。
本发明涉及的高强度钢管,对于该钢管的成分组成、金属组织以及厚度进行了改良。其结果,根据本发明涉及的高强度钢管,能够实现足以作为油井管使用的强度以及韧性。
附图说明
图1是表示钢管的轴向的抗拉强度TS与屈服强度YS的关系的图。
图2是表示本发明涉及的高强度钢管的金属组织的一例的照片。
具体实施方式
以下详细地说明本发明涉及的高强度电焊钢管、高强度电焊钢管用的钢板的制造方法、以及高强度电焊钢管的制造方法的各实施方式。再者,以下所示的“%”,只要没有特别说明就意指“质量%”。另外,“L方向”意指“钢管的轴向”,“C方向”意指“钢管的周向”。
<高强度电焊钢管以及高强度电焊钢管用钢板>
(成分组成)
首先,对本实施方式涉及的高强度电焊钢管(以下有时仅称为“本电焊钢管”)、以及本实施方式涉及的高强度电焊钢管用钢板(以下有时仅称为“本钢板”)的成分组成的限定理由进行说明。
C:0.040~0.070%
C是提高本钢板的淬硬性、提高其强度的元素。当低于0.040%时,得不到所需要的强度,因此C设为0.040%以上。优选为0.045%以上。另一方面,当超过0.070%时,本钢板的韧性、以及钢管的焊接热影响区的韧性降低,因此C设为0.070%以下。优选为0.065%以下。
Si:0.10~0.50%
Si是脱氧元素,也是有助于强度提高的元素。当低于0.10%时,不能充分地得到添加效果,因此Si设为0.10%以上。优选为0.20%以上。另一方面,当超过0.50%时,在电阻焊接时生成含Si的氧化物,焊接部的品质降低,并且焊接热影响区的韧性降低,因此Si设为0.50%以下。优选为0.40%以下。
Mn:1.60~2.00%
Mn是提高本钢板的淬硬性、有助于其强度的提高,并且形成MnS来固定S,抑制铸造时的铸坯裂纹的元素。当低于1.60%时,不能充分地得到添加效果,因此Mn设为1.60%以上。优选为1.70%以上。另一方面,当超过2.00%时,本钢板的耐硫化物应力裂纹性降低,因此Mn设为2.00%以下。优选为1.85%以下。
Nb:0.020~0.080%
Nb是形成微细的碳氮化物,(i)在热轧制后的卷取温度下作为NbC析出从而使本钢板强度提高的元素。另外,Nb是(ii)抑制奥氏体的晶界移动,抑制奥氏体粒的粗大化、再结晶,能够实现热精轧制中的奥氏体未再结晶温度区域轧制,并且防止在奥氏体未再结晶温度区域上方的粗大粒的生成的元素。
当低于0.020%时,不能充分地得到添加效果,因此Nb设为0.020%以上。优选为0.025%以上。另一方面,当超过0.080%时,本钢板的强度过于上升,轧制时的轧制载荷增大,有时精轧制变得困难,因此Nb设为0.080%以下。优选为0.050%以下。
V:0.060%以下
V是形成微细的碳氮化物,不损害焊接性而使本钢板的强度提高的元素。但是,当超过0.060%时,大量地生成碳氮化物,钢板强度上升,另外,有可能韧性降低,因此V设为0.060%以下。优选为0.030%以下。下限值不特别限定,但要充分地得到添加效果的话就优选为0.010%以上。
Ti:0.010~0.025%
Ti是形成氮化物来固定N,防止铸造时的铸坯裂纹的元素。当低于0.010%时,不能充分地得到添加效果,因此Ti设为0.010%以上。优选为0.013%以上。另一方面,当超过0.025%时,大量地生成碳氮化物,钢板的韧性、以及焊接热影响区的韧性降低,因此Ti设为0.025%以下。优选为0.022%以下。
Mo:0.20~0.40%
Mo是除了使淬硬性提高以外还形成碳氮化物从而有助于本钢板的强度提高的元素。当低于0.20%时,不能弥补由C量的降低所致的强度的降低的量,因此Mo设为0.20%以上。优选为0.24%以上。另一方面,当超过0.40%时,大量地生成碳化物,韧性降低,因此Mo设为0.40%以下。优选为0.36%以下。
Ni:0.10~0.50%
Ni是除了有助于本钢板的韧性提高以外还使淬硬性提高的元素。当低于0.10%时,不能充分地得到添加效果,因此Ni设为0.10%以上。优选为0.20%以上。另一方面,当超过0.50%时,钢板的焊接性降低,并且材料成本上升,因此Ni设为0.50%以下。优选为0.45%以下。
Al:0.050%以下
Al是作为脱氧剂发挥作用的元素。但是,当超过0.050%时,大量地生成氧化物,损害钢管的洁净性,因此Al设为0.050%以下。优选为0.030%以下。下限不特别限定,但要充分地得到脱氧效果的话就优选为0.005%以上。更优选为0.010%以上。
3Mo%+Ni%:超过1.00%
在本实施方式中,形成所需要的金属组织(多边形铁素体:10面积%、余量:贝氏体铁素体),该金属组织和成分组成相辅相成,对本电焊钢管给予所需要的机械特性(L方向的抗拉强度:超过725MPa;L方向的屈服强度:655~758MPa;在0℃下C方向的夏比冲击吸收能:22J以上)。为此,在本实施方式中,关于成分组成,作为用于实现上述机械特性的指标,采用强度提高元素Mo的比例与韧性提高元素Ni的比例的和。
Mo是在本电焊钢管中通过由淬硬性的提高带来的组织强化和析出强化、来弥补由低C所致的强度的降低量的重要元素,因此按3Mo来进行评价,组入到上述指标中。而且,在本电焊钢管中,将3Mo%+Ni%设为超过1.00%。
当3Mo%+Ni%为1.00%以下时,变得难以形成所需要的金属组织,因此3Mo%+Ni%设为超过1.00。优选为1.20%以上。关于上限值,由于由各元素的上限值决定,因此不限定。
本电焊钢管以及本钢板的成分组成,除了以上所示的元素以外,还可以含有P:0.030%、S:0.004%以下、N:0.006%以下、O:0.004%以下、和Cu:0.10~0.50%之中的至少任一种。
P:0.030%以下
P是杂质元素,是在晶界偏析从而使耐硫化物应力裂纹性增大的元素。当超过0.030%时,耐硫化物应力裂纹性显著地显现,因此P设为0.030%以下。优选为0.015%以下。下限包括0%,但若将P降低到低于0.005%,则制造成本大幅度上升,因此关于实用钢板以及实用钢管,0.005%为实质的下限值。
S:0.004%以下
S是杂质元素,是使韧性降低、并且形成MnS从而使耐硫化物应力裂纹性增大的元素。当超过0.004%时,钢板的韧性的降低、耐硫化物应力裂纹性显著地显现,因此S设为0.004%以下。优选为0.002%以下。下限包括0%,但若将S降低到低于0.0005%,则制造成本大幅度上升,因此关于实用钢板以及实用钢管,0.0005%为实质的下限值。
N:0.006%以下
N是杂质元素,是通过时效而使造管时的钢板的成形性降低的元素。当超过0.006%时,钢板的成形性的降低显著,因此N设为0.006%以下。优选为0.003%以下。下限包括0%,但若将N降低到低于0.0005%,则制造成本大幅度上升,因此关于实用钢板以及实用钢管,0.0005%为实质的下限值。
O:0.004%以下
O是在本电焊钢管的焊接部形成成为焊接缺陷的原因的氧化物,使焊接部的韧性降低,并且使耐硫化物应力裂纹性增大的元素。当超过0.004%时,焊接部的韧性的降低、以及耐硫化物应力裂纹性的增大显著,因此O设为0.004%以下。优选为0.002%以下。下限包括0%,但若将O降低到低于0.0005%,则制造成本大幅度上升,因此关于实用钢板以及实用钢管,0.0005%为实质的下限值。
Cu:0.10~0.50%
Cu是除了使淬硬性提高以外还通过固溶强化或者析出强化而有助于本钢板强度提高的元素。当低于0.10%时,不能充分地得到添加效果,因此Cu设为0.10%以上。优选为0.15%以上。另一方面,当超过0.50%时,热加工性降低,因此Cu设为0.50%以下。优选为0.45%以下。
再者,在本实施方式中,在含有Cu的情况下也形成所需要的金属组织(多边形铁素体:10面积%、余量:贝氏体铁素体),该金属组织和成分组成相辅相成,对本电焊钢管给予所需要的机械特性(L方向的抗拉强度:超过725MPa;L方向的屈服强度:655~758MPa;在0℃下C方向的夏比冲击吸收能:22J以上)。为此,在本实施方式中,关于成分组成,作为用于实现上述机械特性的指标,采用强度提高元素Mo、Cu的比例、以及韧性提高元素Ni的比例的和。即,在含有Cu的情况下,将(3Mo%+Ni%+Cu%)设为超过1.20%。
Cu是在本电焊钢管中通过组织强化、与固溶强化或析出强化来弥补由低C所致的强度的降低量的重要元素,因此组入到上述指标中。而且,在含有Cu的本电焊钢管中,将3Mo%+Ni%+Cu%设为超过1.20%。
当3Mo%+Ni%+Cu%为1.20%以下时,变得难以形成所需要的金属组织,因此3Mo%+Ni%+Cu%设为超过1.20。优选为1.40%以上。关于上限值,由于由各元素的上限决定,因此不限定。
本实施方式涉及的电焊钢管以及本实施方式涉及的电焊钢管用钢板,除了以上所示的元素以外,还可以在不损害机械特性的范围内含有Ca:0.0040%以下、Cr:0.50%以下、和REM:0.0050%以下之中的至少1种。
Ca:0.0040%以下
Ca是将伸展的粗大的硫化物球化,有助于韧性提高的元素。但是,当超过0.0040%时,钢管的洁净度降低,因此Ca优选为0.0040%以下。更优选为0.0025%以下。下限包括0%,但要充分地得到添加效果的话就优选为0.0005%以上。
Cr:0.50%以下
Cr是提高淬硬性、有助于本钢板的强度提高的元素。但是,当超过0.50%时,在(电阻)焊接时有时诱发焊接缺陷,因此Cr优选为0.50%以下。更优选为0.30%以下。下限包括0%,但要得到添加效果的话就优选为0.05%以上。
REM:0.0050%以下
REM是将伸展的粗大的硫化物球化,有助于韧性的提高的元素。但是,当超过0.0050%时,钢管的洁净度降低,因此REM优选为0.0050%以下。更优选为0.0035%以下。下限包括0%,但要充分地得到添加效果的话就优选为0.0005%以上。
以上对本电焊钢管以及本钢板的成分组成进行了说明,但成分组成的余量为Fe以及不可避免的杂质。在此,所谓不可避免的杂质,是指原材料中所含的、或在制造的过程中混入的成分,并不是有意地使钢含有的成分。另外,所谓不可避免的杂质,具体地可例举出Sb、Sn、W、Co、As、Mg、Pb、Bi、B、以及H。
(金属组织)
接着,对本实施方式涉及的高强度电焊钢管、以及本实施方式涉及的高强度电焊钢管用钢板的金属组织的限定理由进行说明。
在本电焊钢管中,为了切实地确保L方向的抗拉强度:超过725MPa、以及L方向的屈服强度:655~758MPa、而且在0℃下C方向的夏比冲击吸收能:22J以上的机械特性,将金属组织设为10面积%以下的多边形铁素体和余量的贝氏体铁素体的金属组织。
在此,在本实施方式中,所谓多边形铁素体,是指维氏硬度Hv在下述(1)式所示的范围中的金属组织。
Hv=α+430×[C%](200≤α≤240) (1)
而且,在本电焊钢管中,通过将(3Mo%+Ni%)设为超过1.00%、或者将(3Mo%+Ni%+Cu%)设为超过1.20%的组成限定,来稳定地形成上述金属组织,能够确保L方向的抗拉强度:超过725MPa、L方向的屈服强度:655~758MPa、而且0℃的C方向的夏比冲击吸收能:22J以上。关于其原因在后面叙述。
在本电焊钢管的金属组织中,当多边形铁素体超过10面积%时,变得难以担负超过725MPa的抗拉强度的任务,因此多边形铁素体设为10面积%以下。优选为5面积%以下。由于多边形铁素体的面积%因冷却条件而变动,因此多边形铁素体的面积%的下限不作限定。
多边形铁素体的平均粒径优选为20μm以下。当多边形铁素体的平均粒径超过20μm时,有可能本钢板的抗拉强度以及韧性降低。因此,多边形铁素体的平均粒径优选为20μm以下。更优选为15μm以下。
在本实施方式中,所谓金属组织,是指在钢管的母材部,将下述点作为基准点的情况下,以上述基准点为中心在厚度方向的两侧具有0.5mm的宽度的区域中的金属组织,所述点是作为在厚度方向上距外表面的距离为厚度的1/4的点而规定的点。另外,所谓母材部是指从焊接部沿C方向旋转了90度处的钢管的部分。
如果在钢管的上述区域中,形成10面积%以下的多边形铁素体以及余量的贝氏体铁素体的金属组织,则在本电焊钢管中能实现上述机械特性(L方向的抗拉强度:超过725MPa;L方向的屈服强度:655~758MPa;0℃的C方向的夏比冲击吸收能:22J以上)。
在此,所谓面积%意指通过光学显微镜观察而观察到的情况下的面积%。多边形铁素体的平均粒径,是通过对采用光学显微镜观察到的图像进行图像处理,根据多边形铁素体的面积和总数作为等效圆(当量圆)的平均粒径而求出的。
在本钢管中,通过限定成分组成(3Mo%+Ni%:超过1.00,或者3Mo%+Ni%+Cu%:1.20%),可稳定地形成特定的金属组织,进而可实现所希望的机械特性的原因如下。
本钢板的强度,主要地除了贝氏体铁素体的强度以外还通过由卷取时的等温保持时析出的Mo的碳化物引起的析出强化来得到。
关于Mo的析出强化,以约650℃下的等温保持为峰呈现。但是,若进行650℃下的卷取,则变得难以在不生成多边形铁素体的超过5℃/秒的冷却速度下开始相变。
因此,为了尽量避免多边形铁素体的生成,稳定地得到贝氏体铁素体为主体的组织,需要适度提高淬硬性。另一方面,Mo的析出会使钢板的韧性降低,因此Mo的利用需要控制在必要最低限度。
从以上的观点来看,如果关于淬硬性提高元素Mo、Ni、Cu,在(3Mo%+Ni%):超过1.00%的条件、或者(3Mo%+Ni%+Cu%):超过1.20%的条件下添加,则能够尽量防止多边形铁素体的生成。其结果,能够在不损害钢板的韧性的范围内利用Mo的析出强化,来得到目标的抗拉强度。
再者,在将钢板成形来制造钢管的情况下,在成形过程中钢板加工硬化,造管后的钢管的强度上升。由加工硬化引起的强度的上升量依赖于钢板的成形性和加工度而变动,因此不能一概而定,但在造管后的钢管中,为了确保所需要的机械特性,需要考虑由加工硬化引起的强度的上升量来制造钢板。
<高强度电焊钢管用钢板的制造方法以及高强度电焊钢管的制造方法>
接着,对本实施方式涉及的高强度电焊钢管用钢板的制造方法(以下有时仅称为“本钢板的制法”)以及本实施方式涉及的高强度电焊钢管的制造方法(以下有时仅称为“本电焊钢管的制法”)进行说明。
(本钢板的制法)
在本钢板的制法中,将具有上述的本电焊钢管的成分组成(特定组成)的热轧钢板在790℃以上进行热轧,以8~15℃/秒的平均冷却速度冷却,在550~630℃进行卷取,并且,在相变开始时以超过5℃/秒的冷却速度将热轧钢板冷却。
在本钢板的制法中,通过上述的热轧温度、平均冷却速度、卷取温度、以及冷却速度来使作用效果相辅相成,从而本钢板的金属组织成为10面积%以下的多边形铁素体以及余量的贝氏体铁素体。
使用的热轧钢板,是通过将上述特定组成的钢液采用通常的铸造法(优选为连铸法)铸造得到铸坯,并将该铸坯进行热轧制从而得到的热轧钢板。再者,可以将铸坯在铸造后原样地直接进行热轧制,也可以将铸坯暂且冷却后,再次加热到规定的温度来进行热轧制。铸坯的加热温度优选为1150~1300℃。
热轧条件可以是通常的热轧条件,但当热轧结束温度低于790℃时,轧制负荷过度增大,热轧制变得困难,生产率降低,因此热轧结束温度设为790℃以上。优选为800℃以上。
关于热轧制中的累计压下率,在后面的冷却时的相变开始时控制冷却速度,切实地得到规定的金属组织的基础上,950℃以下的累计压下率优选设为50%以上。
在超过950℃的温度区域的热轧中,奥氏体再结晶,因此当超过950℃的温度区域的压下率高时,热轧制结束时的奥氏体相中的位错密度变小,变得难以得到规定的金属组织。
当950℃以下的累计压下率低于50%时,贝氏体铁素体的粒径粗大化,不仅韧性降低,而且在多边形铁素体析出了的情况下,难以使其平均粒径成为20μm以下。更优选950℃以下的累计压下率为65%以上。
热轧结束后,将热轧钢板在ROT(输出辊道:Run Out Table)上冷却,在500~630℃进行卷取。在直到将热轧钢板进行卷取为止的期间,以8~15℃/秒的平均冷却速度将热轧钢板冷却。该冷却时,在热轧钢板的金属组织开始相变时以超过5℃/秒的冷却速度将热轧钢板冷却。
热轧钢板的卷取温度设为500~630℃。当卷取温度低于500℃时,钢板的抗拉强度过度上升,卷取变得困难,因此卷取温度设为500℃以上。优选为550℃以上。另一方面,当卷取温度超过630℃时,难以使相变开始时的冷却速度成为5℃/秒以上,会生成粗大的多边形铁素体,因此卷取温度设为630℃以下。优选为610℃以下。
另外,直到将热轧钢板进行卷取为止的平均冷却速度设为8~15℃/秒。当平均冷却速度低于8℃/秒时,难以使相变开始时的冷却速度成为5℃/秒以上,因此该平均冷却速度设为8℃/秒以上。优选为10℃/秒以上。
另一方面,当平均冷却速度超过15℃/秒时,卷取温度变得低于500℃,钢板的强度过于上升,不仅难以卷取,而且有可能造管变得困难,因此热轧钢板的平均冷却速度设为15℃/秒以下。优选为13℃/秒以下。
再者,当在热轧结束后直到在500~630℃进行卷取为止的期间将热轧钢板以8~15℃/秒的平均冷却速度冷却时,在即将卷取热轧钢板前,热轧钢板的温度达到相变开始温度(具体而言,低于665℃)。
当相变开始时的冷却速度为5℃/秒以下时,容易生成多边形铁素体,难以使多边形铁素体的平均粒径为20μm以下、面积率为10面积%以下,因此相变开始时的冷却速度设为超过5℃/秒。优选为10℃/秒以上。当相变开始时的冷却速度过快时,抗拉强度过于增高,但如果平均冷却速度为15℃/秒以下,则相变开始时的冷却速度不会过快,因此相变开始时的冷却速度的上限值不作限定。
在热轧钢板的温度在即将卷取前达到了相变开始温度的情况下,若以超过5℃/秒的冷却速度将热轧钢板冷却,则能够形成所需要的金属组织(多边形铁素体:10面积%以下、余量:贝氏体铁素体)。其原因如下。
相变开始温度随冷却速度的上升而降低。本钢板的制法中的相变开始温度,在将相变开始时的冷却速度设为5℃/秒的情况下,约为665℃。如果相变开始温度下降到665℃,则难以生成多边形铁素体。另一方面,本钢板由于C量低,因此淬硬性不高,因此在以15℃/秒冷却了的情况下,相变开始温度也约为665℃,贝氏体铁素体成为主体的金属组织。因此,根据本钢板的制法,能够形成多边形铁素体少的、主要由贝氏体铁素体构成的金属组织。
(本电焊钢管的制法)
本电焊钢管,使用本钢板,通过冷加工而成形为管状,将钢板端部对接,进行电阻焊接而得到。冷加工条件不限定于特定的加工条件,可应用通常的加工条件。不对管整体实施热处理,但在焊接部,将外表面加热到950~1050℃,加热后,以使内表面的冷却速度为8℃/秒以上的条件冷却到外表面的冷却停止温度600~450℃。
焊接部的热处理,通常通过采用高频加热,从钢管的外表面侧进行加热,从外表面侧进行水冷来进行。当焊接部的外表面的加热温度低于950℃时,在钢管的管厚度厚的情况下,有时不能够直到焊接部的内表面加热到Ac3点以上的温度,因此焊接部的外表面的加热温度设为950℃以上。优选为970℃以上。
另一方面,当焊接部的外表面的加热温度超过1050℃时,焊接部的晶粒粗大化,韧性降低,因此焊接部的外表面的加热温度设为1050℃以下。优选为1000℃以下。加热时间不作特别限定。
加热后的冷却速度,在焊接部的内表面若低于8℃/秒,则在焊接部过度地生成多边形铁素体,不能得到贝氏体铁素体为主体的金属组织,机械特性降低,因此焊接部的内表面的冷却速度设为8℃/秒以上。优选为15℃/秒以上。
焊接部的内表面的冷却速度的上限设为不会生成上贝氏体的冷却速度。再者,在焊接部的内表面确定冷却速度的下限是因为,冷却是通过从焊接部的外表面水冷来进行的,越向焊接部的内表面侧,冷却速度越慢。
当焊接部的外表面的冷却停止温度超过600℃时,在焊接部难以得到所需要的抗拉强度,因此焊接部的外表面的冷却停止温度设为600℃以下。优选为550℃以下。另一方面,当焊接部的外表面的冷却停止温度低于450℃时,焊接部的强度过于上升,韧性降低,因此焊接部的外表面的冷却停止温度设为450℃以上。优选为480℃以上。
通过该热处理,在焊接部也能够与钢管的母材部同样地实现规定的机械特性(L方向的抗拉强度:超过725MPa,L方向的屈服强度:655~758MPa,而且,在0℃下C方向的夏比冲击值:22J以上)。
根据以上所述,在将本钢板成形为管状并进行电阻焊接,进而实施规定的热处理,来得到本电焊钢管的情况下,在焊接部能够确保与钢管的母材部同样的机械特性。因此,能够成品率良好地制造适合作为用于例如导向套管(conductor)、表层套管(surfacecasing)的油井管的、壁厚15mm以上、外径300mm以上的高强度电焊钢管。
实施例
接着,对本发明的实施例进行说明。在实施例中设定的条件是为了确认本发明的可实施性以及效果而采用的一条件例,本发明并不被该一条件例限定。本发明可在不脱离本发明的要旨、能达到本发明的目的的限度下采用各种条件。
(实施例1)
将表1所示的成分组成1~13的各成分的钢液进行连铸而得到钢坯,按照表2所示的制造条件记号a的各条件制得热轧钢板,其后在冷态下将钢板成形为管状,对钢板端部进行电阻焊接,得到外径473mm的钢管。再者,表1中的指标Z是(3Mo%+Ni%)或者(3Mo%+Ni%+Cu%)。
表1
表2
从制造出的钢管的母材部制取试样,将L方向的截面作为观察面,用光学显微镜观察金属组织,测定了多边形铁素体的平均粒径。另外,测定了钢管的L方向的抗拉强度TS、钢管的L方向的0.5%耐力YS(产生0.5%的残余应变时的屈服强度),对于母材部测定了0℃的C方向的夏比冲击吸收能。其结果示于表3。
表3
(注)BF:贝氏体铁素体;PF:多边形铁素体
另外,在图1中示出按照表2的各制造条件记号制造的钢管的L方向中的抗拉强度TS和屈服强度YS。再者,在图1中,在本发明范围的框内标记的矩形记号表示实施例,在本发明范围的框外标记的×记号表示比较例。根据图1可知,对于本电焊钢管,得到了以下结果:抗拉强度超过725MPa、以及屈服强度为655~758MPa。
(实施例2)
将表1所示的成分组成1的钢液进行连铸而得到钢坯,按照表2所示的制造条件记号a~k的各条件制得热轧钢板,其后,在冷态下将钢板成形为管状,对钢板端部进行电阻焊接,得到外径473mm的钢管。
从制造出的钢管的母材部以及焊接部制取试样,将L方向的截面作为观察面,用光学显微镜观察金属组织,测定了多边形铁素体的平均粒径。另外,测定了钢管的L方向的抗拉强度TS、钢管的L方向的0.5%耐力YS,对于母材部以及焊接部分别测定了0℃的C方向的夏比冲击吸收能(J)。将其结果示于表4。再者,拉伸试验按照ASTM A370进行,夏比冲击吸收能的测定按照ASTM A370以及ASTM E23进行。
表4
(注)BF:贝氏体铁素体;UB:上贝氏体
而且,在图2中示出按照表4的制造条件记号a制造的本电焊钢管的金属组织。根据图2可知,对于本电焊钢管,得到了由10面积%以下的多边形铁素体和余量的贝氏体铁素体组成的金属组织。
Claims (13)
1.一种高强度电焊钢管,其特征在于,
成分组成以质量%计含有
C:0.040~0.070%、
Si:0.10~0.50%、
Mn:1.60~2.00%、
Nb:0.020~0.080%、
V:0.060%以下、
Ti:0.010~0.025%、
Mo:0.20~0.40%、
Ni:0.10~0.50%、
Al:0.050%以下、
3Mo%+Ni%:超过1.00%,
余量包含Fe以及不可避免的杂质,
在钢管的母材部,将下述点作为基准点的情况下,以所述基准点为中心在厚度方向的两侧具有0.5mm的宽度的区域中的金属组织由10面积%以下的多边形铁素体和余量的贝氏体铁素体构成,所述点是作为在厚度方向上距外表面的距离为厚度的1/4的点而规定的点,
厚度为15.0~19.8mm,
所述多边形铁素体,是指维氏硬度Hv在下式所示的范围中的金属组织:Hv=α+430×[C%],其中200≤α≤240。
2.根据权利要求1所述的高强度电焊钢管,
所述成分组成以质量%计还含有
P:0.030%以下、
S:0.004%以下、
N:0.006%以下、
O:0.004%以下。
3.根据权利要求1所述的高强度电焊钢管,
所述成分组成以质量%计还含有
Cu:0.10~0.50%、
Cr:0.05~0.50%、
Ca:0.0005~0.0040%、
REM:0.0005~0.0050%
之中的一种或两种以上。
4.根据权利要求2所述的高强度电焊钢管,
所述成分组成以质量%计还含有
Cu:0.10~0.50%、
Cr:0.05~0.50%、
Ca:0.0005~0.0040%、
REM:0.0005~0.0050%
之中的一种或两种以上。
5.根据权利要求3所述的高强度电焊钢管,
3Mo%+Ni%+Cu%超过1.20%。
6.根据权利要求4所述的高强度电焊钢管,
3Mo%+Ni%+Cu%超过1.20%。
7.根据权利要求1~6的任一项所述的高强度电焊钢管,
所述多边形铁素体的平均粒径为20μm以下。
8.根据权利要求1~6的任一项所述的高强度电焊钢管,
所述金属组织的机械特性是:轴向的抗拉强度超过725MPa;轴向的屈服强度为655~758MPa;在0℃下周向的夏比冲击吸收能为22J以上。
9.根据权利要求7所述的高强度电焊钢管,
所述金属组织的机械特性是:轴向的抗拉强度超过725MPa;轴向的屈服强度为655~758MPa;在0℃下周向的夏比冲击吸收能为22J以上。
10.一种高强度电焊钢管用钢板的制造方法,其特征在于,
将具有权利要求1~4的任一项中所述的成分组成的热轧钢板在热轧结束温度790℃以上进行热轧,以8~15℃/秒的平均冷却速度冷却,在500~630℃进行卷取,并且,在相变开始时以超过5℃/秒的冷却速度冷却。
11.根据权利要求10所述的高强度电焊钢管用钢板的制造方法,
所述相变开始时的温度低于665℃。
12.根据权利要求10或11所述的高强度电焊钢管用钢板的制造方法,
所述热轧钢板是将铸坯加热并实施950℃以下的累计压下率为50%以上的热轧制而得到的热轧钢板。
13.一种高强度电焊钢管的制造方法,其特征在于,
将采用权利要求10~12的任一项所述的方法制造的钢板成形为管状,对所述钢板的端部进行电阻焊接,并将焊接部的外表面加热到950~1050℃,以使焊接部的内表面的冷却速度为8℃/秒以上的条件冷却到所述外表面的冷却停止温度600~450℃。
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