CN117089682A - 一种csp产线成形性能优良的纳米析出高强钢及其生产方法 - Google Patents
一种csp产线成形性能优良的纳米析出高强钢及其生产方法 Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 80
- 239000010959 steel Substances 0.000 title claims abstract description 80
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 37
- 238000005096 rolling process Methods 0.000 claims abstract description 40
- 238000000034 method Methods 0.000 claims abstract description 24
- 230000008569 process Effects 0.000 claims abstract description 23
- 238000001816 cooling Methods 0.000 claims abstract description 22
- 238000010438 heat treatment Methods 0.000 claims abstract description 13
- 238000007670 refining Methods 0.000 claims abstract description 13
- 238000009749 continuous casting Methods 0.000 claims abstract description 11
- 238000003723 Smelting Methods 0.000 claims abstract description 7
- 238000010583 slow cooling Methods 0.000 claims abstract description 6
- 238000005266 casting Methods 0.000 claims abstract description 5
- 238000005275 alloying Methods 0.000 claims abstract description 4
- 238000002791 soaking Methods 0.000 claims abstract description 4
- 230000009467 reduction Effects 0.000 claims description 13
- 239000000126 substance Substances 0.000 claims description 11
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 10
- 229910052799 carbon Inorganic materials 0.000 claims description 10
- 239000012535 impurity Substances 0.000 claims description 7
- 229910001208 Crucible steel Inorganic materials 0.000 claims description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 3
- 230000000704 physical effect Effects 0.000 abstract description 2
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- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 6
- 229910052748 manganese Inorganic materials 0.000 description 6
- 229910000859 α-Fe Inorganic materials 0.000 description 6
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
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- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 4
- 229910052750 molybdenum Inorganic materials 0.000 description 4
- 239000011733 molybdenum Substances 0.000 description 4
- 229910052710 silicon Inorganic materials 0.000 description 4
- 239000010703 silicon Substances 0.000 description 4
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
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- RQNWIZPPADIBDY-UHFFFAOYSA-N arsenic atom Chemical compound [As] RQNWIZPPADIBDY-UHFFFAOYSA-N 0.000 description 2
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- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910000742 Microalloyed steel Inorganic materials 0.000 description 1
- 229910004283 SiO 4 Inorganic materials 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
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- 125000004432 carbon atom Chemical group C* 0.000 description 1
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- 238000004886 process control Methods 0.000 description 1
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- 229910052720 vanadium Inorganic materials 0.000 description 1
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Abstract
本发明公开了一种CSP产线成形性能优良的纳米析出高强钢的生产方法,利用薄板坯连铸连轧工艺生产,具体步骤如下:1)经过转炉冶炼后进入LF炉进行单精炼处理,精炼过程进行合金化处理;2)将钢水进行薄板坯连铸连轧生产,铸坯在均热炉内进行加热;然后在架精轧机中进行轧制;3)层流冷却;4)钢卷进行卷取,同时针对厚度规格≤2.5mm钢卷采用头尾U冷工艺;5)钢卷下线后在钢卷库集中堆垛缓冷。本发明生产的纳米析出高强钢的实物性能如下:屈服强度≥700MPa,抗拉强度≥785MPa,延伸率≥20%,扩孔率≥60%,厚度1.2~4.5mm,不仅具备高强度,同时还具备优良的成形性能。
Description
技术领域
本发明涉及微合金化钢制造领域,具体地指一种利用CSP产线生产厚度规格1.2~4.5mm具备高强度、优良成形和焊接性能的纳米析出高强钢的生产方法。
背景技术
如何通过提高钢板强度实现结构轻量化,从而达到降耗节能,减轻工人劳动强度等效果,已经成为现代钢铁材料发展的必然。对于一般结构用钢,随着材料强度的提升,其成形性能呈下降趋势。成型性能表征着材料变形能力,直接影响用户零件结构的成形,当成形性能不足时容易发生开裂等问题,导致材料不可用。如何解决强度和成形性能这一对矛盾体,也成为钢铁材料品种研究开发的难点。
屈服强度700MPa级高强度钢在国内外机构和企业中都开展了研究和制造。CN1639371A公布的弯曲加工性优良的耐候性高强度钢板及其制造方法,CN1757783A公开了一种700MPa级F/B高强带钢的制造方法,CN101153371A公开了一种高强度冷成型热连轧钢板及其生产方法,其屈服强度都能达到700MPa级,但设计成分中含有Cu、Ni、V、Mo、Nb等较多贵重合金,导致整体生产成本居高不下。如何开发一种同时具备高强度、高成形性能,同时兼具经济性和实用性的低合金高强钢材料,具有相当难度。
发明内容
本发明主要解决的技术问题是依据CSP产线的设备及技术特点,开发一种薄规格纳米析出热轧高强钢,一方面保证高强度(屈服强度≥700MPa,抗拉强度≥785MPa),另一方面具备高成形性能(断后延伸率≥20%,扩孔率≥60%),在此基础上,实现低成本设计和生产。
本发明为解决上述提出的问题所采用的技术方案为:
一种CSP产线成形性能优良的纳米析出高强钢的生产方法,利用薄板坯连铸连轧工艺生产,工艺流程包括:转炉冶炼、LF钢包炉单精炼、薄板坯连铸连轧、层流冷却、卷取、轧后堆垛缓冷,具体步骤如下:
1)经过转炉冶炼后进入LF炉进行单精炼处理,精炼过程进行合金化处理后的钢水的化学成分重量百分比含量:C:0.03~0.06%,Si:≤0.15%,Mn:1.3~1.5%,P:≤0.012%,S:≤0.003%,Ti:0.11~0.15%,Als:0.02~0.06%,Mo:0.05~0.12%,As≤0.012%,N≤0.006%,余量为Fe及不可避免的杂质;
2)将钢水进行薄板坯连铸连轧生产:浇铸的钢坯厚度65~80mm;铸坯在均热炉内进行加热,加热温度控制在1200~1230℃;在7机架精轧机中进行轧制,精轧开轧温度≥1080℃,前三道次压下率≥50%,F4道次压下率≥38%,F5道次压下率≥33%,终轧温度控制在890~930℃;
3)层流冷却:出精轧机后水冷速度为70~120℃/s;
4)卷取:钢卷卷取温度控制在610~650℃(目标卷取温度优选630℃左右)进行卷取,同时针对厚度规格≤2.5mm钢卷采用头尾U冷工艺;
5)钢卷下线后在钢卷库集中堆垛缓冷。
按上述方案,步骤2)中,钢水的化学成分重量百分比含量优选为:C:0.04~0.06%,Si:≤0.12%,Mn:1.45~1.5%,P:≤0.010%,S:≤0.003%,Ti:0.11~0.15%,Als:0.03~0.035%,Mo:0.075~0.09%,As≤0.005%,N≤0.005%,余量为Fe及不可避免的杂质
按上述方案,步骤2)中,钢水的化学成分的碳当量0.3~0.35%。
按上述方案,步骤2)中,轧制厚度1.2~4.5mm;并且,根据成品厚度,轧制速度控制在3.0~12.0m/s进行轧制,是为了保证通卷工艺的稳定性,保证整体性能稳定。
按上述方案,步骤4)中,U冷工艺具体为带钢头部和带钢尾部10米距离内卷取温度设定值在目标卷取温度基础上提高20℃。
上述方法生产的纳米析出高强钢的实物性能如下:屈服强度≥700MPa,抗拉强度≥785MPa,延伸率≥20%,扩孔率≥60%,厚度1.2~4.5mm,不仅具备高强度,同时还具备优良的成形性能。
本发明中主要成分和工艺的改进及机理如下:
碳C:碳是最经济的强化元素。碳含量过高会导致碳化物析出的驱动力增加,不利于材料的成形性能,同时当碳含量接近0.07%时,还会使钢水在浇铸过程中发生包晶反应,增加连铸漏钢风险;碳含量过低,强化效果降低存在性能不满足要求的情况。基于强度以及成形等多方面考虑,将碳含量限定在0.04~0.06%范围。
硅Si:硅可以净化铁素体,避免冷却时粗大碳化物的生成,但是硅也容易形成Fe2SiO4并在钢坯表面与FeO形成共析产物,并凝固成锚状结构,使FeO难以去除,影响最终表面质量。所以将硅含量限定在≤0.12%范围。
锰Mn:锰是提高强度和韧性最有效的元素,可有效的推迟奥氏体转变,起到细化晶粒的效果。如果其含量小于1.30%,不能满足材料强度要求;但是添加过量的锰,同样容易导致钢水包晶反应,造成连铸裂纹等质量问题,同时锰含量对焊接性能影响较大,因此将锰含量限定在1.30~1.50%范围。
钼Mo:钼一方面可以提高材料的淬透性,再加上锰的综合作用,使珠光体和贝氏体转变显著滞后,可以细化组织提升材料的强度和韧性;同时钼是碳化物形成元素,与碳的亲和力较强,可以起到溶质拖拽作用,降低碳原子的扩散速度,阻止纳米级碳化物析出相的进一步长大,显著提升纳米析出强化效果。但钼合金价格较高,添加过多会导致生产成本大幅增加。基于强度和成本综合考虑,在本发明中将钼含量控制在0.05~0.12%。
钛Ti:钛的析出强化效果突出,是保证钢材强度的经济有效元素,Ti合金元素添加量过高容易产生过多的TiN硬质颗粒,影响材料的成形性能,Ti含量添加过少不能满足材料的强度要求,本发明在上述碳含量和锰含量一定的前提下,将钛含量范围设计在0.11~0.15%。
磷P:磷容易产生中心偏析,影响成形性能。在本发明中将磷含量控制在≤0.010%。
铝Als:作为冶炼过程有效的脱氧剂,同时具有一定的细化晶粒作用,提升钢材强度,但也容易形成Al2O3夹杂物。在本发明中将铝含量控制在0.02~0.06%。
砷As:会大幅度降低材料韧塑性,在本发明中将砷含量严格控制在≤0.012%。
硫S、氮N:容易与钢中Ti结合,影响Ti的强化效果,同时会极大影响钢材的塑性,在本发明中将硫控制在≤0.003%,氮控制在≤0.006%。
对本发明主要工艺的控制进行说明如下:
本发明钢坯厚度设定为65-80mm,主要是结合产线轧机负荷和不同成品厚度进行考虑;
加热温度:一方面加热温度越高碳化物等回熔效果越好,但CSP产线加热炉设备特点决定了加热温度有一个1230℃的上限,同时加热温度过高会导致奥氏体晶粒尺寸长大,故本发明将加热温度控制在1200~1230℃;
道次压下率分配成前三道次压下率≥50%,F4道次压下率≥38%,F5道次压下率≥33%,主要是结合成分特点和轧机负荷情况,采取尽可能大的累积变形,破碎铸态枝晶组织,起到均匀化和细化奥氏体晶粒的效果;
层流冷却冷速设定在70~120℃/s,主要是考虑本发明种产品在该冷速范围内,可以尽可能多的发生铁素体转变,同时细化晶粒;
卷取温度设定在610~650℃,同时采用U形冷却工艺主要是从同卷性能均匀性和析出最佳温度范围考虑。在该温度范围可以最大程度发挥Ti的析出强化效果,同时带钢头尾采用U冷工艺可以弥补内外圈冷速过快导致析出不充分而产生的带钢头尾与中间性能的差异,影响材料在用户端的加工稳定性;
根据成品厚度,轧制速度控制在3.0~12.0m/s进行恒速轧制,是为了保证通卷工艺的稳定性,保证整体性能稳定。
相对于现有技术,本发明有益效果如下:
本发明与现有技术相比,产品不仅具备高强度(屈服强度≥700MPa,抗拉强度≥785MPa),同时还具备高成形性(断后延伸率≥20%,扩孔率≥60%)。本发明通过控制C含量在0.04~0.06%,减少碳化物析出保证材料具备良好的延伸率和扩孔性能;同时在C+Mn+Ti成分基础上通过添加适量的Mo来控制析出相的尺寸在10nm范围内,显著提高析出强化效果,且对材料的塑性和韧性影响小;而且,Mo合金元素添加还可以有效降低焊缝热影响区软化,提升材料的应用性能。因此,本发明的纳米析出高强钢产品可以满足用户冲压、辊压、折弯等多种成形工艺,且兼具优良的焊接性能,能够用于汽车零部件等成形性能及服役要求较高的领域,同时还可以用于高强结构件领域。
附图说明
图1和图2分别为本发明的金相组织和纳米析出相形貌图;其中,金相组织类型为铁素体或者铁素体+少量贝氏体。
具体实施方式
为了更好地理解本发明,下面结合实施例进一步阐明本发明的内容,但应当理解,此处所描述的具体实施例仅仅用以解释本发明,并不限定本发明。
实施例1~5
一种CSP产线成形性能优良的纳米析出高强钢的生产方法,利用薄板坯连铸连轧工艺生产,工艺流程包括:转炉冶炼、LF钢包炉单精炼、薄板坯连铸连轧、层流冷却、卷取、轧后堆垛缓冷,具体步骤如下:
1)经过转炉冶炼后进入LF炉进行单精炼处理,精炼过程进行合金化处理后的钢水的化学成分重量百分比含量:C:0.03~0.06%,Si:≤0.15%,Mn:1.3~1.5%,P:≤0.012%,S:≤0.003%,Ti:0.11~0.15%,Als:0.02~0.06%,Mo:0.05~0.12%,As≤0.012%,N≤0.006%,余量为Fe及不可避免的杂质;
2)将钢水进行薄板坯连铸连轧生产:浇铸的钢坯厚度65~80mm;铸坯在均热炉内进行加热,加热温度控制在1200~1230℃;在7机架精轧机中进行轧制,精轧开轧温度≥1080℃,前三道次压下率≥50%,F4道次压下率≥38%,F5道次压下率≥33%,终轧温度控制在890~930℃,轧制速度控制在3.0~12.0m/s,轧制厚度1.2~4.5mm;
3)层流冷却:出精轧机后水冷速度为70~120℃/s;
4)卷取:钢卷卷取温度控制在610~650℃(目标卷取温度优选630℃)进行卷取,同时针对厚度规格≤2.5mm钢卷采用头尾U冷工艺;U冷工艺具体为带钢头部和带钢尾部10米距离内卷取温度设定值在目标卷取温度基础上提高20℃;
5)钢卷下线后在钢卷库集中堆垛缓冷。
表1为本发明各实施例的化学成分列表;表2为本发明各实施例的主要工艺参数及相应性能列表。
表1本发明各实施例的化学成分列表
表2本发明各实施例的主要工艺参数和相应性能列表
从表2可以看出,实施例1-5所得纳米析出高强钢成品满足屈服强度为≥700MPa级,抗拉强度≥785MPa,延伸率≥20%,扩孔率≥60%的要求。本发明产品的金相组织如图1所示,组织类型为铁素体或者铁素体+少量贝氏体,该组织类型具有较好的塑性,可以使得产品满足后续加工过程。产品的析出相如图2所示,析出相分布均匀,尺寸在10nm以内,能够极大提升析出强化效果,且不会对塑性和韧性产生较大影响。
以上所述仅是本发明的优选实施方式,应当指出,对于本领域的普通技术人员来说,在不脱离本发明创造构思的前提下,还可以做出若干改进和变换,这些都属于本发明的保护范围。
Claims (8)
1.一种CSP产线成形性能优良的纳米析出高强钢的生产方法,其特征在于,包括以下步骤:
1)经过转炉冶炼后进入LF炉进行单精炼处理,精炼过程进行合金化处理后的钢水的化学成分重量百分比含量:C:0.03~0.06%,Si:≤0.15%,Mn:1.3~1.5%,P:≤0.012%,S:≤0.003%,Ti:0.11~0.15%,Als:0.02~0.06%,Mo:0.05~0.12%,As≤0.012%,N≤0.006%,余量为Fe及不可避免的杂质;
2)将钢水进行薄板坯连铸连轧生产:浇铸的钢坯厚度65~80mm;铸坯在均热炉内进行加热,加热温度控制在1200~1230℃;在7机架精轧机中进行轧制,精轧开轧温度≥1080℃,前三道次压下率≥50%,F4道次压下率≥38%,F5道次压下率≥33%,终轧温度控制在890~930℃;
3)层流冷却:出精轧机后水冷速度为70~120℃/s;
4)卷取:钢卷卷取温度控制在610~650℃进行卷取,同时针对厚度规格≤2.5mm钢卷采用头尾U冷工艺;
5)钢卷下线后在钢卷库集中堆垛缓冷。
2.根据权利要求1所述的一种CSP产线成形性能优良的纳米析出高强钢的生产方法,其特征在于,步骤2)中,钢水的化学成分重量百分比含量:C:0.04~0.06%,Si:≤0.12%,Mn:1.45~1.5%,P:≤0.010%,S:≤0.003%,Ti:0.11~0.15%,Als:0.03~0.035%,Mo:0.075~0.09%,As≤0.005%,N≤0.005%,余量为Fe及不可避免的杂质。
3.根据权利要求1所述的一种CSP产线成形性能优良的纳米析出高强钢的生产方法,其特征在于,步骤2)中,钢水的化学成分的碳当量0.3~0.35%。
4.根据权利要求1所述的一种CSP产线成形性能优良的纳米析出高强钢的生产方法,其特征在于,步骤2)中,轧制厚度1.2~4.5mm;并且,根据成品厚度,轧制速度控制在3.0~12.0m/s进行轧制。
5.根据权利要求1所述的一种CSP产线成形性能优良的纳米析出高强钢的生产方法,其特征在于,步骤4)中,U冷工艺具体为带钢头部和带钢尾部10米距离内卷取温度设定值在目标卷取温度基础上提高20℃。
6.一种CSP产线成形性能优良的纳米析出高强钢,其特征在于,化学成分重量百分比含量:C:0.03~0.06%,Si:≤0.15%,Mn:1.3~1.5%,P:≤0.012%,S:≤0.003%,Ti:0.11~0.15%,Als:0.02~0.06%,Mo:0.05~0.12%,As≤0.012%,N≤0.006%,余量为Fe及不可避免的杂质。
7.根据权利要求6所述的CSP产线成形性能优良的纳米析出高强钢,其特征在于,化学成分重量百分比含量:C:0.04~0.06%,Si:≤0.12%,Mn:1.45~1.5%,P:≤0.010%,S:≤0.003%,Ti:0.11~0.15%,Als:0.03~0.035%,Mo:0.075~0.09%,As≤0.005%,N≤0.005%,余量为Fe及不可避免的杂质。
8.根据权利要求6所述的CSP产线成形性能优良的纳米析出高强钢,其特征在于,所述纳米析出高强钢的性能如下:屈服强度≥700MPa,抗拉强度≥785MPa,延伸率≥20%,扩孔率≥60%,厚度1.2~4.5mm。
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