CN104126023B - 高强度可烘烤硬化的低密度钢及所述钢的制备方法 - Google Patents
高强度可烘烤硬化的低密度钢及所述钢的制备方法 Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 69
- 239000010959 steel Substances 0.000 title claims abstract description 69
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 8
- 229910052799 carbon Inorganic materials 0.000 claims description 30
- 229910052719 titanium Inorganic materials 0.000 claims description 19
- 238000000137 annealing Methods 0.000 claims description 14
- 229910052757 nitrogen Inorganic materials 0.000 claims description 13
- 238000000034 method Methods 0.000 claims description 11
- 238000005097 cold rolling Methods 0.000 claims description 9
- 238000005246 galvanizing Methods 0.000 claims description 9
- 238000005098 hot rolling Methods 0.000 claims description 7
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- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 6
- 229910052782 aluminium Inorganic materials 0.000 claims description 6
- 229910052751 metal Inorganic materials 0.000 claims description 6
- 239000002184 metal Substances 0.000 claims description 6
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- 239000012535 impurity Substances 0.000 claims description 5
- 229910052758 niobium Inorganic materials 0.000 claims description 5
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- 229910052726 zirconium Inorganic materials 0.000 claims description 5
- 239000011248 coating agent Substances 0.000 claims description 4
- 238000009749 continuous casting Methods 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 229910052717 sulfur Inorganic materials 0.000 claims description 4
- 238000004804 winding Methods 0.000 claims description 4
- 238000005266 casting Methods 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims description 3
- 238000010438 heat treatment Methods 0.000 claims description 2
- 238000001816 cooling Methods 0.000 claims 2
- 230000005484 gravity Effects 0.000 claims 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 26
- 239000010936 titanium Substances 0.000 description 23
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 20
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- 239000010955 niobium Substances 0.000 description 12
- 239000006104 solid solution Substances 0.000 description 10
- 239000000203 mixture Substances 0.000 description 8
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 6
- 230000032683 aging Effects 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 239000011572 manganese Substances 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 229910052791 calcium Inorganic materials 0.000 description 3
- 239000011575 calcium Substances 0.000 description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- 239000004411 aluminium Substances 0.000 description 2
- 229910052796 boron Inorganic materials 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 230000002269 spontaneous effect Effects 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 229910001335 Galvanized steel Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 150000001721 carbon Chemical class 0.000 description 1
- DXHPZXWIPWDXHJ-UHFFFAOYSA-N carbon monosulfide Chemical class [S+]#[C-] DXHPZXWIPWDXHJ-UHFFFAOYSA-N 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
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- 239000000446 fuel Substances 0.000 description 1
- 239000008397 galvanized steel Substances 0.000 description 1
- 238000010348 incorporation Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- QJGQUHMNIGDVPM-UHFFFAOYSA-N nitrogen group Chemical group [N] QJGQUHMNIGDVPM-UHFFFAOYSA-N 0.000 description 1
- 238000010422 painting Methods 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 238000007669 thermal treatment Methods 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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Abstract
本发明涉及一种高强度可烘烤硬化的低密度钢及其制备方法。
Description
技术领域
本发明涉及高强度可烘烤硬化的低密度钢及所述钢的制备方法。
背景技术
在减少车辆的碳排放的持续努力中,钢铁行业连同汽车制造商持续寻求允许重量降低而不影响钢的加工性能和成品的安全性的钢。为了满足未来的CO2排放要求,必须减少机动车的燃料消耗。为了这种减少的一种方法是降低车体的重量。具有低密度和高强度的钢可以有助于此。在相同厚度下,低密度钢的使用降低汽车部件的重量。伴随着已知高强度钢的一个问题是它们的高强度损害了在片材成形为汽车部件过程中材料的可成形性。
普通高强度钢例如双相钢,允许使用较薄的片材并且因此降低重量。但是,较薄的零件将对其它性质例如刚度、防撞性和抗凹陷性产生负面影响。这些负面影响只能通过增加钢的厚度来解决,这从而否定了降低厚度(downgauging)的效果,或通过改变部件的几何形状来解决,这也是不希望的。
发明内容
本发明的一个目的是提供一种低密度钢,其在成品部件中具有高强度,并在形成汽车部件之前结合具有优良的可成形性。
本发明的另一个目的是提供一种具有优良的刚度和抗凹陷性的高强度钢。
可以通过提供一种铁素体钢带材或片材来实现这些目的中的一个或多个,所述的铁素体钢带材或片材以重量百分比计包括:
·最多 0.01%C_总量;
·最多 0.5%Si;
·最多 1.0%Mn;
·从5到最多 10%的Al;
·最多 0.010%N;
·最多 0.019%Ti;
·最多 0.08%Nb;
·最多 0.1%Zr;
·最多 0.1%V;
·最多 0.01%S;
·最多 0.1%P;
·任选在5和50ppm之间的B;
·余量为铁和不可避免的杂质;
其中C_溶质=C_总量
-最小值[X,Y]
-最大值[Z,0]
-12/93*Nb
-12/91*Zr
-12/51*V;
其中
·X=2*12/(2*32)*S;
·Y=2*12/(4*48)*(Ti-48/14*N);
·Z=12/48*(Ti-48/14*N-4*48/(2*32)*S);
其中,
最小值[X,Y]=X和Y的较低值,并且如果Y是负数,那么最小值[X,Y]=0;
最大值[Z,0]=0和Z的较高值;
并且其中C_溶质为至少0.0005(5ppm)。
所有百分比均以重量百分比计,除非另有说明。为了避免任何误解,当在商用电子表格程序例如Microsoft Excel中键入时,以上给出的式子将导致式子的正确解释。例如将12/93*Nb正确解释为(12/93)*Nb,因为技术人员将认识到该式子中的碳(12)和Nb(93)的原子质量。这对于该式子中的其它数字是相同的(作了必要的修正)。因此,不必要地:
根据本发明的钢具有特制的化学组成,以使得钢在退火和任选的镀锌步骤后含有在固溶体中的碳(C_溶质)。这种在固溶体中的碳允许例如在涂漆-烘烤周期中钢为可烘烤硬化的。汽车部件由来自轧机的钢成形,并且在将该部件成形为其最终形状后将其涂漆并烘烤。
此外,根据本发明的钢将在形成汽车部件之前即在涂漆-烘烤操作之前的良好可成形性与在涂漆-烘烤操作之后的较高强度结合。
发明人发现,对于在涂漆-烘烤周期中是可烘烤硬化的钢,至少5ppm的溶质碳(C_溶质)必须存在于钢中。在更低量的溶质碳下,该效果是可忽略或不可重现的。
溶质碳的水平还不可超过临界上限值,因为钢优选免于自然时效。自然失效是在室温下过饱和固溶体的自发时效,并涉及钢的物理性质的自发变化,其在热轧或冷轧后或最终热处理之后(例如在处理该带材之前运输至客户或储存在客户处的过程中)将钢保持在大气温度下时发生。这种自然时效涉及被认为是不需要的机械性质变化,因为它们在汽车部件的成形过程中会引起加工性能不可预测的改变。此外,由于所谓的Lüder-线的形成,还可不利地影响表面品质。另外,在固溶体中过高的碳水平可导致在烘烤硬化之前可成形性的劣化。
由于这个原因,溶质碳的最大值为50ppm是优选的。更合适的最大值为40ppm的溶质碳(即0.004%)。
具体实施方案
在本发明的一个实施方案中,C_溶质为至少0.0010(10ppm)和/或至多0.0030(30ppm)。这获得了稳定的过程和可重现的性质。
氮,尤其是游离氮(即固溶体中的氮)在炼钢中不需要但不可避免。可以任选地添加钛以将氮结合为TiN。钢中大量的铝也可以确保结合所有氮。这意味着该基质在固溶体中基本上不含氮。
在钢中任选地添加硼。其存在不是强制的,但是其可以有助于抑制二次加工脆化的任何倾向。如果添加,那么需要的最小量为5ppm的硼。
在本发明的一个实施方案中,锰含量为至少0.1%。在另一个实施方案中,铝含量为至少6%和/或至多9%,优选为至多8%。
优选对该钢进行钙处理。因此,化学组成还可以包含与钙处理一致的量的钙。
在根据本发明的钢中,通过添加微合金元素(Ti、Nb、V、Zr)结合在该钢中总碳含量的优良控制来控制固溶体中的碳量。
Ti或Nb的量应该严格控制。太多的钛或铌将与碳结合以形成碳化物或(在硫存在下)碳硫化物。因为这一结果,没有溶质碳是可得到的并且没有可烘烤硬化性。
根据本发明的固溶体中的碳量是通过从总碳含量C_总量减去析出物中包含的碳计算如下:
C_溶质=C_总量
-最小值[X,Y]
-最大值[Z,0]
-12/93*Nb
-12/91*Zr
-12/51*V;
其中
X=2*12/(2*32)*S;
Y=2*12/(4*48)*(Ti-48/14*N);
Z=12/48*(Ti-48/14*N-4*48/(2*32)*S);
其中
最小值[X,Y]=X和Y的较低值,并且如果Y是负数,那么最小值[X,Y]=0;
最大值[Z,0]=0和Z的较高值。
对于这些式子的解释见上文。添加Ti有益于结合氮,但不是严格必需的。可以在该钢中添加最多0.019%的Ti,以主要将氮结合为TiN并且其次控制溶质碳的量。钛含量必须0.019%或更低,例如至多0.018%或0.015%或甚至至多0.012%。
如果作为合金化元素添加钛,那么对于钛含量合适的最小值为0.005%。如果添加,那么对于Nb合适的最小值为0.008%。如果添加,
那么对于V和Zr合适的最小值分别为0.002和0.004。
根据一个优选的实施方案,根据本发明的铁素体钢的组成具有基本组成(以重量百分比计):
·0.01%C_总量;
·最多 0.5%Si;
·最多 1.0%Mn;
·从5到最多 10%的Al;
·最多 0.010%N;
·最多 0.08%Nb;
·最多 0.1%Zr;
·最多 0.1%V;
·最多 0.01%S;
·最多 0.1%P;
·任选在5和50ppm之间的B;
·余量为铁和不可避免的杂质;
在这个组成中,在钢中没有添加钛,并且存在的任何钛均是不可避免的杂质。
钛,作为合金化元素或作为不可避免的杂质,将首先形成TiN。如果存在过量的氮,那么残余的氮将与铝结合。如果存在过量的钛,那么残余的钛将形成Ti4C2S2直到消耗所有的钛。最小值[X,Y]因子计算了在将所有游离氮结合为TiN以后通过形成Ti4C2S2消耗了多少碳。如果对于Y该计算导致负值,那么将该因子设置为零。
如果完全不存在钛,那么将不会形成TiN或Ti4C2S2并且最小值[X,Y]等于零。最大值[Z,0]因子决定了在考虑TiN和Ti4C2S2的形成后多少碳与钛结合。其它三个因子考虑了NbC、ZrC和VC的形成,并且由此连同最小值[X,Y]因子和最大值[Z,0]因子一起确定钢中溶质碳的量。
通过不添加或仅添加少量的钛和/或指定量的Nb,将存在足够的可用于烘烤硬化的溶质碳。通过控制溶质碳的水平低于50ppm,并且优选低于40ppm,根据本发明的钢是可烘烤硬化并抗自然时效的。
根据第二方面,提供了一种用于制备铁素体钢带材的方法,包括步骤:
·通过以下方式提供钢板坯或厚带材:
ο连铸,或
ο通过薄板坯连铸,或
ο通过带式连铸,或
ο通过带坯连铸;
·任选地随后通过在至多1250℃的再加热温度下再加热该钢板坯或带材;
·热轧该板坯或厚带材并且在至少850℃的热终轧温度下完成热轧过程;
·在550和750℃之间的卷绕温度下卷绕该热轧带材。
在优选的实施方案中,该卷绕温度为至少600℃和/或该热终轧温度为至少900℃。
随后可以在包括如下步骤的方法中进一步处理该热轧带材:
·以40-90%的冷轧压下量冷轧该热轧带材以制备冷轧带材;
·在具有700和900℃之间的峰值金属温度的连续退火过程中退火该冷轧带材;
·任选地在热浸镀锌或电镀锌或加热涂覆(heat-to-coat)过程中将该退火的钢带材镀锌。
在冷轧步骤前通常酸洗和清洗该热轧带材。在一个实施方案中,连续退火过程中的峰值金属温度为至少750℃,优选至少800℃。
在一个实施方案中,该冷轧压下量为至少50%。
在一个实施方案中,该热轧带材的厚度在1和5mm之间和/或该冷轧带材的厚度在0.4和2mm之间。
在发明的一个实施方案中,将该热轧带材在连续退火步骤中退火并且任选在热浸镀锌步骤中镀锌。该退火还可以在所谓的加热涂覆周期中进行。在加热涂覆周期中,将该热轧钢再加热至足以进行热浸镀锌的温度,但不是加热至与常规连续退火步骤一样高的温度。在再加热的过程中,将在热轧后热轧卷材的缓冷过程中可析出的碳再次带入固溶体中。在退火和/或镀锌以后,必须快速冷却该钢以避免固溶体中碳的析出。当通过成形然后是涂漆和烘烤使用这种镀锌钢片材用于制造汽车部件或其它产品时,则该涂漆-烘烤还确保了与涂漆-烘烤周期相关的强度增加。
现在通过下述的非限制性实施例进一步解释本发明。
将钢制备和处理成厚度为1mm的冷轧钢片材。该冷轧带材的厚度为3.0mm。在表1中给出了该钢的化学组成。
表1—化学组成(I=发明,R=参考)
钢 | C | Al | Mn | N | Ti | Nb | S | C_溶质 | |
1 | 0.0020 | 7.0 | 0.20 | 0.0035 | 0.000 | 0.000 | 0.004 | 0.0020 | I |
2 | 0.0020 | 7.0 | 0.20 | 0.0030 | 0.010 | 0.000 | 0.004 | 0.0020 | I |
3 | 0.0040 | 7.0 | 0.20 | 0.0030 | 0.000 | 0.020 | 0.004 | 0.0014 | I |
3a | 0.0040 | 6.9 | 0.20 | 0.0025 | 0.005 | 0.010 | 0.001 | 0.0031 | I |
4 | 0.0030 | 8.0 | 0.20 | 0.0030 | 0.010 | 0.010 | 0.004 | 0.0017 | I |
5 | 0.0040 | 7.5 | 0.20 | 0.0040 | 0.000 | 0.020 | 0.004 | 0.0014 | I |
6 | 0.0050 | 6.5 | 0.25 | 0.0030 | 0.010 | 0.020 | 0.004 | 0.0024 | I |
7 | 0.0050 | 6.0 | 0.20 | 0.0030 | 0.010 | 0.040 | 0.005 | 0.0000 | R |
8 | 0.0050 | 6.8 | 0.20 | 0.0030 | 0.100 | 0.000 | 0.005 | 0.0000 | R |
9 | 0.0050 | 7.0 | 0.20 | 0.0030 | 0.010 | 0.050 | 0.005 | 0.0000 | R |
通过铸造板坯和在至多1250℃的温度下再加热该板坯来制备该钢。这个温度是最高温度,因为在更高的再加热温度下可发生过度的晶粒生长。在热轧过程中的终轧温度为900℃,卷绕温度650℃,接着酸洗和冷轧(67%)并且在800℃的峰值金属温度下连续退火以及热浸镀锌。钢3a还含有16ppm的B。
表2—涂漆-烘烤周期前后的机械性质
WH=由于2%预应变的加工硬化
BH=由于在170℃20分钟的烘烤-硬化
在表2中给出的结果清楚地表明,在14至24或至31ppm的水平下的溶质碳的存在导致在加工硬化和钢的基体强度上约40MPa的增加。发明人发现这样的效果存在于5和50ppm之间的溶质碳水平下。
Claims (20)
1.铁素体钢带材或片材,以重量百分比计由如下组成:
最多0.01%C_总量;
最多0.5%Si;
0.1-1.0%Mn;
从5到9%的Al;
最多0.010%N;
最多0.01%S;
最多0.1%P;
以下的至少一种:
0.005-0.019%Ti;
0.008-0.08%Nb;
0.002-0.1%V;
0.004-0.1%Zr;
任选在5和50ppm之间的B;
余量为铁和不可避免的杂质;
其中C_溶质=C_总量
-最小值[X,Y]
-最大值[Z,0]
-(12/93)*Nb
-(12/91)*Zr
-(12/51)*V;
其中
其中,
最小值[X,Y]=X和Y的较低值,并且如果Y是负数,那么最小值[X,Y]=0;
最大值[Z,0]=0和Z的较高值;
并且其中C_溶质为至少5ppm。
2.根据权利要求1所述的铁素体钢带材或片材,其中C_溶质为至多50ppm。
3.根据权利要求1或2所述的铁素体钢带材或片材,其中Mn为至少0.1%。
4.根据权利要求1或2所述的铁素体钢带材或片材,其中Al为至少6%和至多9%。
5.根据权利要求4所述的铁素体钢带材或片材,其中Al为至少6%和至多8%。
6.根据权利要求1或2所述的铁素体钢带材或片材,其中C_总量为至少0.0010%(10ppm)。
7.根据权利要求1或2所述的铁素体钢带材或片材,其中C_溶质为至少0.0010%(10ppm)和至多0.0040%(40ppm)。
8.根据权利要求7所述的铁素体钢带材或片材,其中C_溶质为至少0.0010%(10ppm)和至多0.0030%(30ppm)。
9.根据权利要求1或2所述的铁素体钢带材或片材,其中N为至多0.005%(50ppm)。
10.根据权利要求1或2所述的铁素体钢带材或片材,其中Si为至多0.2%。
11.根据权利要求1或2所述的铁素体钢带材或片材,其中该钢的比重在6800和7300kg/m3之间。
12.根据权利要求1或2所述的铁素体钢带材或片材,其中C_溶质为至多0.0040%(40ppm)。
13.根据权利要求1或2所述的铁素体钢带材或片材,其中C_溶质为至少0.0010%(10ppm)。
14.制备根据权利要求1-13中任一项所述的铁素体钢带材的方法,包括步骤:
·通过以下方式提供钢板坯或厚带材:
o连铸,或
o通过薄板坯连铸,或
o通过带式连铸,或
o通过带坯连铸;
·任选地随后通过在至多1250℃的再加热温度下再加热该钢板坯或带材;
·热轧该板坯或厚带材并且在至少850℃的热终轧温度下完成热轧过程;
·在550和750℃之间的卷绕温度下卷绕该热轧带材。
15.根据权利要求14所述的方法,其中在下述步骤中再加热该热轧带材:
·连续退火步骤,任选随后热浸镀锌接着快冷,或
·加热涂覆步骤,随后热浸镀锌和快冷。
16.制造铁素体钢带材的方法,包括步骤:
·以40-90%的冷轧压下量冷轧权利要求14所述的铁素体钢带材以制备冷轧带材;
·在具有700和900℃之间的峰值金属温度的连续退火过程中退火该冷轧带材;
·任选地在热浸镀锌或电镀锌或加热涂覆过程中将该退火的带材镀锌。
17.根据权利要求16所述的方法,其中在连续退火过程中的峰值金属温度为至少750℃。
18.根据权利要求16所述的方法,其中在连续退火过程中的峰值金属温度为至少800℃。
19.根据权利要求16至18中任一项所述的方法,其中冷轧压下量为至少50%。
20.根据权利要求16至18中任一项所述的方法,其中热轧带材的厚度在1和5mm之间和/或其中冷轧带材的厚度在0.4和2mm之间。
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JPH04252229A (ja) | 1991-01-29 | 1992-09-08 | Asahi Chem Ind Co Ltd | シリコーン化合物及びその製法 |
KR0121737B1 (ko) | 1992-08-31 | 1997-12-04 | 다나까 미노루 | 소부 경화성, 상온 비시효성 및 가공성이 우수한 냉연강판 및 용융아연 도금 냉연강판 및 그의 제조방법 |
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JP2001271148A (ja) * | 2000-03-27 | 2001-10-02 | Nisshin Steel Co Ltd | 耐高温酸化性に優れた高Al鋼板 |
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