CN115572895B - 一种hb500级高冷弯型耐磨钢及生产方法 - Google Patents
一种hb500级高冷弯型耐磨钢及生产方法 Download PDFInfo
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Abstract
本发明公开了一种HB500级高冷弯型耐磨钢,化学成分按重量百分比为:C:0.15~0.30%,Si:0~0.08%,Mn:1.0~4.0%,P≤0.015%,S≤0.005%,Als:0.03~0.06%,Ti:0.005~0.03%,Cr:0.4~1.0%,Mo:0~0.3%,其余为Fe及杂质;包括冶炼、连铸、加热、粗轧、精轧、冷却、卷取、横切工艺;加热工艺中,二加和均热末段温度1250~1300℃,二加和均热时间≥70min,总在炉时间控制在≥150min;粗轧工艺中出口温度1050℃~1110℃,中间坯厚度30mm~50mm;精轧工艺中开轧温度950℃~1050℃,精轧终轧温度890℃~920℃;冷却工艺中,出FT7后空冷2~3s至820~860℃后,采用超高冷速100~300℃0s冷却至600℃~750℃后,再空冷2~10s,之后以冷却速度50~100℃0s冷却至150℃~300℃卷取。
Description
技术领域
本发明属于冶金技术领域,具体涉及一种HB500级高冷弯型耐磨钢及生产方法。
背景技术
低合金高强度耐磨钢因其合金含量低、生产灵活方便、价格便宜等特点而被广泛应用于冶金、矿山、建材、铁路、电力、煤炭等机械装备中,使用环境恶劣,对于成形性、耐磨性等提出了严苛要求,商用车等下游用户产品不断升级换代,对于耐磨钢成形性的要求不断增加,传统调质耐磨钢在折弯等应用加工方面面临的挑战日益提高,成为限制耐磨钢在自卸车等下游行业推广的瓶颈所在。
公开号CN1109919A的发明专利提供了一种低合金耐磨钢,其成分重量百分比为:C: 0.5~0.6%,Si:0.9~1.2%,Mn:1.4~1.7%,Cr:1.35~1.60%,Mo:0.3~0.5%,V:0.05~0.10%, Ti:0.03~0.06%,Re:0.02~0.04%,强度和耐磨性均较好,但大量添加提高淬透性的合金元素,成本较高,且C、Si含量高易产生淬火裂纹,易导致冷弯开裂,影响用户使用。
公开号CN102605234A提供了一种HB400级耐磨钢板及其制造方法,其成分重量百分比为:C:0.08~0.24%,Si:0.1~0.3%,Mn:0.7~1.7%,Cr:1.0%,Mo:0.6%,B:0.0005~0.004%, Ti:0.005~0.04%,其余为Fe和微量杂质元素,采用铸造-控轧-调质热处理工艺生产,性能优良,适用于制造工程机械中易磨损设备,不足之处在于调质热处理工艺成本较高和生产周期较长,未对冷弯性能进行针对性设计,含有Mo等贵重元素,合金成本高。
可见,现有耐磨钢存在合金成本高、工艺控制复杂、成形性能不适应下游用户越来越高的使用要求等技术难题,因此有必要进行成分工艺设计,提高冷弯成形性能。
发明内容
本发明目的在于一种HB500级高冷弯型耐磨钢及其生产方法,工艺控制简便,不含Nb 等贵重元素,可达D=5a,180°合格,适用于多种应用环境。
为达到上述目的,采用技术方案如下:
一种HB500级高冷弯型耐磨钢,其化学成分按重量百分比为:C:0.15~0.30%,Si:0~0.08%, Mn:1.0~4.0%,P≤0.015%,S≤0.005%,Als:0.03~0.06%,Ti:0.005~0.03%,Cr:0.4~1.0%, Mo:0~0.3%,其余为Fe及杂质。
上述HB500级高冷弯型耐磨钢的生产方法,包括冶炼、连铸、加热、粗轧、精轧、冷却、卷取、横切工艺。
按上述方案,加热工艺中,二加和均热末段温度1250~1300℃,二加和均热时间≥70min,总在炉时间控制在≥150min。
按上述方案,粗轧工艺中出口温度1050℃~1110℃,中间坯厚度30mm~50mm。
按上述方案,精轧工艺中开轧温度950℃~1050℃,精轧终轧温度890℃~920℃。
按上述方案,冷却工艺中,采用两段空冷+两段水冷方式进行,出FT7后空冷2~3s至 820~860℃后,采用超高冷速100~300℃0s冷却至600℃~750℃后,再空冷2~10s,之后以冷却速度50~100℃0s冷却至150℃~300℃卷取。
本发明中成分范围及工艺要点设置原因如下:
C是提高材料强度最廉价的元素,随着含碳量增加,硬度、强度提高,但塑韧性和焊接性能降低。综合考虑,C重量百分含量为0.15~0.30%即可;
Si能降低碳在铁素体中的扩散速度,促进铁素体形成,也会恶化表面质量。综合考虑, Si重量百分含量为0.00~0.08%为宜;
Mn显著降低Ar1温度、奥氏体分解速度,提高过冷奥氏体稳定性,促进奥氏体释放应力,增加最终组织中的残奥含量,提高冷弯性能,但Mn含量若太高,会增加回火脆性,导致严重中心偏析,综合考虑,Mn重量百分含量为1.0~4.0%为宜。
Als在钢中可脱氧,降低夹杂物含量,也能起到细化晶粒的作用,综合考虑,Als在0.03~0.06%;
Ti在钢的凝固过程中能与N结合生成稳定的TiN,可强烈阻碍奥氏体晶界迁移,从而细化奥氏体晶粒。综合考虑,Ti重量百分含量为0.005~0.03%为宜;
Cr能提高淬透性,也能提高回火稳定性,降低得到马氏体的冷速,但过高的Cr降低加工性和焊接性,综合考虑,Cr重量百分含量为0.4%~1.0%为宜;
Mo显著抑制贝氏体和铁素体转变,提高淬透性,细化晶粒,提高回火稳定性,综合考虑,Mo重量百分含量为0~0.3%为宜;
P、S是钢中有害的杂质元素,钢中P易在钢中形成偏析,降低钢的韧性和焊接性能,S 易形成塑性硫化物,使钢板产生分层,恶化钢板性能,故P、S含量越低越好,综合考虑,将钢的P、S含量为P≤0.015%,S≤0.005%。
相对于现有技术,本发明有益效果如下:
本发明在加热工艺中二加和均热末段温度1250~1300℃,二加+均热时间≥70min,总在炉时间控制在≥150min。保证合金元素完全固溶及充分奥氏体化,在保证板坯温度均匀的同时,为后期回复和应力释放提供稳定的奥氏体晶粒,有利于转变成马氏体后,提升马氏体的冷弯性能。
冷却是控制板形和性能的关键,空冷的目的在于给予奥氏体和过冷奥氏体充分的释放应力时间,使得转变成马氏体后的应力水平降低,冷弯性能提高。卷取温度如果高于300℃,卷取后冷却速度较慢,钢卷处于回火状态,随着卷取温度提高,板条马氏体转变为回火马氏体、回火索氏体甚至回火屈氏体,强度、硬度将逐步显著降低,无法满足性能要求,卷取温度如果过低,钢卷冷后无法自回火,内应力无法有效消除,钢板内应力不均匀,在折弯成型等应用过程中,极易发生因内应力过大导致的折弯开裂问题。本发明采用150℃~300℃卷取温度,会发生一定的自回火,进一步降低内应力水平,提高冷弯性能,强度和硬度略微下降,但总体不变。
本发明成分工艺设计简单,不含Nb等贵重元素,大大降低了成本。
本发明所得HB500级高冷弯型耐磨钢可达D=5a,180°合格,冷弯性能优异,适用于多种应用环境。
附图说明
图1:实施例1所得HB500级高冷弯型耐磨钢冷弯实物图。
具体实施方式
以下实施例进一步阐释本发明的技术方案,但不作为对本发明保护范围的限制。
具体实施方式提供了一种HB500级高冷弯型耐磨钢,其化学成分按重量百分比为:C: 0.15~0.30%,Si:0~0.08%,Mn:1.0~4.0%,P≤0.015%,S≤0.005%,Als:0.03~0.06%,Ti: 0.005~0.03%,Cr:0.4~1.0%,Mo:0~0.3%,其余为Fe及杂质。
具体实施方式还提供了上述HB500级高冷弯型耐磨钢的生产方法,包括冶炼、连铸、加热、粗轧、精轧、冷却、卷取、横切工艺;
具体地,加热工艺中,二加和均热末段温度1250~1300℃,二加+均热时间≥70min,总在炉时间控制在≥150min,保证合金元素完全固溶及充分奥氏体化,在保证板坯温度均匀的同时,为后期回复和应力释放提供稳定的奥氏体晶粒,有利于转变成马氏体后,提升马氏体的冷弯性能。
粗轧工艺中,粗轧出口温度1050℃~1110℃,中间坯厚度30mm~50mm。
精轧工艺中,精轧开轧温度950℃~1050℃,精轧终轧温度890℃~920℃。
冷却工艺中,冷却工艺中,采用两段空冷+两段水冷方式进行,出FT7后空冷2~3s至 820~860℃后,采用超高冷速100~300℃0s冷却至600℃~750℃后,再空冷2~10s,之后以冷却速度50~100℃0s冷却至150℃~300℃卷取。
本发明HB500级高冷弯型耐磨钢实施例1-10各化学成分及其重量百分比如表1所示,传统耐磨钢对比例1-2具体各化学成分及其重量百分比也如表1所示。
表1
C0% | Si0% | Mn0% | P0% | S0% | Als0% | Nb0% | Ti0% | Cr0% | Mo0% | |
实施例1 | 0.3 | 0.04 | 2 | 0.006 | 0.005 | 0.06 | — | 0.017 | 0.4 | 0 |
实施例2 | 0.22 | 0.01 | 4 | 0.009 | 0.002 | 0.06 | — | 0.008 | 0.4 | 0 |
实施例3 | 0.17 | 0.01 | 1 | 0.008 | 0.005 | 0.03 | — | 0.029 | 0.5 | 0.1 |
实施例4 | 0.3 | 0.03 | 1 | 0.008 | 0.005 | 0.05 | — | 0.013 | 1 | 0 |
实施例5 | 0.27 | 0.06 | 2 | 0.009 | 0.002 | 0.03 | — | 0.022 | 0.4 | 0.3 |
实施例6 | 0.23 | 0 | 3 | 0.008 | 0.005 | 0.06 | — | 0.03 | 0.5 | 0.3 |
实施例7 | 0.2 | 0.01 | 4 | 0.007 | 0.003 | 0.06 | — | 0.018 | 1 | 0.2 |
实施例8 | 0.27 | 0 | 1 | 0.008 | 0.005 | 0.04 | — | 0.009 | 0.4 | 0 |
实施例9 | 0.15 | 0.07 | 4 | 0.01 | 0.003 | 0.05 | — | 0.023 | 0.5 | 0 |
实施例10 | 0.15 | 0.02 | 2 | 0.011 | 0.004 | 0.04 | — | 0.028 | 0.4 | 0.3 |
对比例1 | 0.16 | 0.35 | 1.55 | 0.01 | 0.003 | 0.021 | 0.02 | 0.033 | 0.2 | 0.6 |
对比例2 | 0.27 | 0.3 | 1.85 | 0.009 | 0.002 | 0.045 | 0.031 | 0.051 | 0.1 | 0.45 |
实施例1-10和对比例1-2中生产工艺特征的具体工艺数据见表2、表3。
表2
表3
根据GB0T228和GB0T231国家标准,测试实施例1-10所得易加工高强钢以及对比例1-2 的性能如表4所示。实施例1所得高冷弯型耐磨钢冷弯实物图见附图1所示。
可见,实施例1-10在强度更高的情况下,冷弯性能更优,而对比例中强度低,冷弯性能仅能满足D=4a,180°合格,说明实施例冷弯性能更加优异。
表4
实施例 | 屈服强度0MPa | 抗拉强度0MPa | A0% | 冷弯性能 |
实施例1 | 1358 | 1622 | 10.7 | D=5a,180°合格 |
实施例2 | 1302 | 1670 | 10.8 | D=5a,180°合格 |
实施例3 | 1309 | 1673 | 10.3 | D=5a,180°合格 |
实施例4 | 1355 | 1649 | 10.3 | D=5a,180°合格 |
实施例5 | 1381 | 1625 | 10.8 | D=5a,180°合格 |
实施例6 | 1351 | 1661 | 10.7 | D=5a,180°合格 |
实施例7 | 1312 | 1653 | 10.1 | D=5a,180°合格 |
实施例8 | 1365 | 1680 | 10 | D=5a,180°合格 |
实施例9 | 1335 | 1666 | 10.9 | D=5a,180°合格 |
实施例10 | 1333 | 1655 | 10.1 | D=5a,180°合格 |
对比例1 | 1250 | 1450 | 10 | D=4a,90°合格 |
对比例2 | 1211 | 1430 | 11.1 | D=4a,90°合格 |
以上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 (1)
1.一种HB500级高冷弯型耐磨钢,其特征在于化学成分按重量百分比为:C:0.15~0.30%,Si:0~0.08%,Mn:1.0~4.0%,P≤0.015%,S≤0.005%,Als:0.03~0.06%,Ti:0.005~0.03%,Cr:0.4~1.0%,Mo:0~0.3%,其余为Fe及杂质;
所述HB500级高冷弯型耐磨钢通过冶炼、连铸、加热、粗轧、精轧、冷却、卷取、横切工艺制备而来;
其中,加热工艺中,二加和均热末段温度1250~1300℃,二加和均热时间≥70min,总在炉时间控制在≥150min;
粗轧工艺中出口温度1050℃~1110℃,中间坯厚度30mm~50mm;
精轧工艺中开轧温度950℃~1050℃,精轧终轧温度890℃~920℃;
冷却工艺中,采用两段空冷+两段水冷方式进行,出FT7后空冷2~3s至820~860℃后,采用超高冷速100~300℃/s冷却至600℃~750℃后,再空冷2~10s,之后以冷却速度50~100℃/s冷却至150℃~300℃卷取。
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