CN105543701A - 低锰高铬抗hic管线用针状铁素体钢及其制造方法 - Google Patents
低锰高铬抗hic管线用针状铁素体钢及其制造方法 Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 98
- 239000010959 steel Substances 0.000 title claims abstract description 98
- 239000011572 manganese Substances 0.000 title claims abstract description 26
- 239000011651 chromium Substances 0.000 title claims abstract description 21
- 229910000859 α-Fe Inorganic materials 0.000 title claims abstract description 21
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 17
- 229910052739 hydrogen Inorganic materials 0.000 title claims abstract description 13
- 239000001257 hydrogen Substances 0.000 title claims abstract description 13
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 title claims abstract description 12
- 229910052804 chromium Inorganic materials 0.000 title claims abstract description 11
- 229910052748 manganese Inorganic materials 0.000 title claims abstract description 11
- 238000005336 cracking Methods 0.000 title abstract description 7
- 238000000034 method Methods 0.000 claims abstract description 32
- 238000005096 rolling process Methods 0.000 claims abstract description 24
- 238000001816 cooling Methods 0.000 claims abstract description 23
- 230000008569 process Effects 0.000 claims abstract description 16
- 238000003723 Smelting Methods 0.000 claims abstract description 11
- 238000010438 heat treatment Methods 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 238000005266 casting Methods 0.000 claims abstract description 7
- 238000007670 refining Methods 0.000 claims abstract description 6
- 239000000126 substance Substances 0.000 claims abstract description 6
- 229910052782 aluminium Inorganic materials 0.000 claims description 18
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 16
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 16
- 239000004411 aluminium Substances 0.000 claims description 12
- 239000011575 calcium Substances 0.000 claims description 12
- 238000001953 recrystallisation Methods 0.000 claims description 12
- 238000007664 blowing Methods 0.000 claims description 9
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 8
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 8
- 229910052786 argon Inorganic materials 0.000 claims description 8
- 238000005516 engineering process Methods 0.000 claims description 7
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- 229910000616 Ferromanganese Inorganic materials 0.000 claims description 3
- DALUDRGQOYMVLD-UHFFFAOYSA-N iron manganese Chemical compound [Mn].[Fe] DALUDRGQOYMVLD-UHFFFAOYSA-N 0.000 claims description 3
- 238000002791 soaking Methods 0.000 claims description 3
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims description 2
- 235000008733 Citrus aurantifolia Nutrition 0.000 claims description 2
- 241001062472 Stokellia anisodon Species 0.000 claims description 2
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- 229910052791 calcium Inorganic materials 0.000 claims description 2
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- 238000009792 diffusion process Methods 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
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- 238000012546 transfer Methods 0.000 description 2
- 101100294112 Caenorhabditis elegans nhr-47 gene Proteins 0.000 description 1
- RWSOTUBLDIXVET-UHFFFAOYSA-N Dihydrogen sulfide Chemical compound S RWSOTUBLDIXVET-UHFFFAOYSA-N 0.000 description 1
- 101100222704 Neurospora crassa (strain ATCC 24698 / 74-OR23-1A / CBS 708.71 / DSM 1257 / FGSC 987) csr-1 gene Proteins 0.000 description 1
- 238000004873 anchoring Methods 0.000 description 1
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- 230000008878 coupling Effects 0.000 description 1
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- 239000008367 deionised water Substances 0.000 description 1
- 229910021641 deionized water Inorganic materials 0.000 description 1
- 230000003009 desulfurizing effect Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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Abstract
一种低锰高铬抗HIC管线用针状铁素体钢及其制造方法,属于铁素体钢技术领域。化学成分重量百分比C:0.03%~0.05%;Si:0.30%~0.50%;Mn:0.30%~0.50%;Cr:0.50%~1.20%;Alt:0.015%~0.050%;Nb:0.050%~0.080%;Ti:0.010%~0.020%;Ca:0.0020%~0.0040%;P:≤0.012%;S:≤0.0080%;N:≤0.0060%,其余为Fe及不可避免杂质;通过铁水脱硫扒渣、转炉冶炼、LF炉精炼、RH真空处理、板坯浇铸、板坯加热、钢板轧制、ACC层流冷却的冶炼工艺完成。优点在于:力学及抗HIC性能优良。
Description
技术领域
本发明属于铁素体钢技术领域,特别涉及一种低锰高铬抗HIC管线用针状铁素体钢及其制造方法。
背景技术
随着石油天然气需求量的不断增加,为增加其输送效率,管线输送压力也相应增大。我国石油天然气中H2S含量一般较低,在输送压力较低时,可通过脱硫后作为甜气(PH2S≤300Pa)使用。当输气压力提高时,若使H2S的分压PH2S≤300Pa,则必须降低H2S的输入浓度,这给脱硫处理带来较大困难。H2S腐蚀主要有两种形式:氢致开裂(HydrogenInducedCracking-HIC)和应力腐蚀开裂(StressCorrosionCracking-SCC)。本文侧重抗HIC管线用钢性能与组织的研究。H2S对管线钢基体的腐蚀除受诸多环境因素的影响(如环境温度、H2S分压、介质中水的含量、PH值及Cl-含量等),管线材料本身的化学成分、显微组织、夹杂物及带状组织等对HIC影响较大。随着输送压力的不断提高,H2S腐蚀及应力腐蚀问题也必将越来越严重,原来低压输送中认为是非酸性的介质,在如今的高压输送中极有可能造成氢致开裂或应力腐蚀。
我国目前的管线管钢级水平己达到X80,正在进行更高钢级开发。随着高强度管线管的开发和应用,母材、焊缝强度和硬度均有所增加,其产生氢致开裂和应力腐蚀破裂的可能性也就相应增加。油气田开发前期认为是干的、非酸性气体,在开发后期会因含水量的增加而成为湿H2S酸性气体,从而使输送管线有可能受到氢损伤的威胁。在国外,随着高纯净、低硫抗HIC管线钢的开发,虽然HIC行为得到了抑制,但同时应力腐蚀敏感性却有所增加。
一般情况下,在C含量相同的情况下,随着Mn含量的增加,强度增加且脆性转变温度下降。但Mn含量过高,会使韧性降低,造成钢板带状组织严重,增强各向异性,降低抗氢致裂纹(HIC)性能。Cr含量对钢的抗硫化性能的影响很大,钢中Cr含量愈多,S对钢的相对腐蚀就愈小。Cr的强化机制略不同于Mo,它促进M/A岛的生成,而非针状体素体或贝氏体,故可以降低屈服延伸。当Cr与轧制后的加速冷却时同样可得到针状体素体和贝氏体组织。与Mn相比,Ni和Cu缩小δ体素体温度范围,Cr则保持δ体素体相范围和增加连铸坯在高温δ相区的停留时间,该区的扩散速率高于奥氏体区,这有利于提高溶质的扩散,促进铸造组织偏析的再分布。另外,抗HIC管线钢对杂质元素S、P要求极为严格,增加钢水冶炼过程难度,同时增加工序成本,对设备处理能力要求也较高。在微观组织方面,针状铁素体组织对抗HIC性能较为有利,铁素体及珠光体对HIC比较敏感,这归因于针状铁素体组织致密,互相交织,位错密度大。高密度位错是强烈的氢陷阱,为氢的重新分布提供许多位置,可避免局部区域产生高的氢压而发生微观裂纹;被沉淀析出相钉轧的位错可为氢陷阱。
对比专利“CN100359035C-酸性环境用X65管线钢及其制造方法”,通过以下成分体系,C:0.02-0.05%;Mn:1.20-1.50%;Si:0.10-0.50%;P:≤0.012%;S:≤0.002%;Nb:0.05-0.07%;Ti:0.005-0.0.025%;Mo:0.050-0.195%;Cu:≤0.35%;Ni:≤0.35%;N:≤0.0080%;Ca:0.0015-0.0045%;Ca/S≥2.0。该专利采用常规的钢水冶炼、钢坯浇铸、一般热轧工艺及轧后卷取等流程,生产X65级别管线钢。该专利对S含量要求较为严格,并需要控制Ca/S比,增加钢水冶炼的困难;同时,该专利加入一定量贵重合金,如Ni、Mo等,增加生产成本。
对比专利“CN102301015B-耐HIC性优良的厚壁高强度热轧钢板及其制造方法”,含有C:0.02-0.08%;Mn:0.50-1.85%;Nb:0.03-0.10%;Ti:0.001-0.05%;B:0.0005%以下,且满足(Ti+Nb/2)/C<4,或者还含有Ca:0.010%以下;Rem:0.02%以下中的一种或两种,余量由Fe及的杂质构成,生产含贝氏体铁素体相或贝氏体相,并且表层硬度以维氏硬度计为230HV以下。该专利Mn含量范围0.50-1.85%,对其它合金Ni、Cr、Mo、Cu等无严格限制,成分范围较为宽泛。同时该专利中要求,在精轧结束后依次三道冷却工序;第一冷却工序:以20℃/s以上且小于马氏体生成临界冷却速度的平均冷却速度进行加速冷却,直至所述热轧板表面的表面温度达到Ar3相变点以下且Ms点以上;第二冷却工序:急冷至板厚中心达到350℃以上且低于600℃的温度范围的温度;第三冷却工序:在以板厚中心的温度计为350℃以上且低于600℃的温度范围的卷取温度下卷取成卷状后,实施冷却以使至少卷厚度方向的1/4板厚~3/4板厚的位置在350℃~600℃的温度范围内保持或滞留30分钟。此专利成分范围极为宽泛,且冷却工艺较为复杂,不一定具备批量工业化生产条件。
对于抗HIC管线用钢,钢水冶炼、钢板轧制、微观组织及力学性能等,对其抗HIC性能均有较大影响,如何均衡其相互关系,在成本不显著增加的前提下,生产力学性能优良,且具有较好抗HIC性能管线用钢,值得深入研究。
发明内容
本发明的目的在于提供一种低锰高铬抗HIC管线用针状铁素体钢及其制造方法,解决了在成本不显著增加的前提下,生产具有优良力学性能及较好抗HIC性能管线用钢的问题。
一种低锰高铬抗HIC管线用针状铁素体钢,其化学成分重量百分比为,C:0.03%~0.05%;Si:0.30%~0.50%;Mn:0.30%~0.50%;Cr:0.50%~1.20%;Alt:0.015%~0.050%;Nb:0.050%~0.080%;Ti:0.010%~0.020%;Ca:0.0020%~0.0040%;P:≤0.012%;S:≤0.0080%;N:≤0.0060%,其余为Fe及不可避免杂质。
一种低锰高铬抗HIC管线用针状铁素体钢的制造方法,通过铁水脱硫扒渣、转炉冶炼、LF炉精炼、RH真空处理、板坯浇铸、板坯加热、钢板轧制、ACC层流冷却的钢水冶炼工艺路线完成。其步骤及参数控制如下:
1、钢水冶炼过程中温度控制参数如下:参考液相线温度1521℃;转炉出钢1650±20℃;LF结束1635±10℃,第一炉1650±10℃;RH结束1585±5℃,第一炉1595±10℃;软吹结束温度1565±5℃;中包温度1540±5℃。
2、冶炼:采用底吹氩A模式,转炉吹炼初期底吹氩气流量设定为400m3/h、吹炼末期底吹氩气流量设定为500m3/h。
3、转炉出钢:出钢1/3时,随钢流加入白灰2.4kg~2.6kg/吨钢水、萤石0.045kg~0.055kg/吨钢水进行渣洗;出钢完毕后在渣面加铝篦子0.025kg~0.035kg/吨钢水,铝篦子拆开加入,保证钢包底吹效果,确保铝篦子与渣反应。
4、LF炉精炼:精炼过程用低碳锰铁调Mn,其中C:0.20%~0.70%;Mn:80.0%~90.0%;其余为杂质S、P;处理过程禁止用铝铁脱氧及调铝,使用铝粒调铝,LF结束铝按照0.040%~0.050%控制,LF炉总调铝量不超过5kg/吨钢水,出LF炉前加入钛铁调Ti,参考吸收率80%~85%。
5、RH真空处理:提升Ar流量800~1200NL/min,进行钢水脱氢,保证深真空处理时间≥12min,其中最后一批合金调整完成之后,要求真空处理时间≥5min,期间测温、取样、微调成份;真空结束进行定氢;每炉钢水喂入350米SiCa线及200米Ca线,并保证钢水中Ca含量在25~30ppm之间,根据钢中钙含量调整;吊包前对钢水进行软吹,软吹氩气流量控制在≤100L/min,渣面不得翻开,保证钢水软吹时间≥12min;软吹后钢水镇静时间≥5min。
6、连铸过程,300mm厚连铸坯:拉速范围:0.75m/min~0.85m/min;目标:0.80m/min,并采用动态轻压下技术,目标保证铸坯低倍中心偏析≤C类1.0级。
7、钢坯加热:采用步进梁式加热炉将钢坯加热至设定均热温度1160℃~1220℃,钢坯在炉时间260min~360min,300mm厚规格钢坯目标在炉加热时间320min,以保证钢坯充分奥氏体化。
8、钢板控轧控冷:采用再结晶区及非再结晶区两阶段轧制,并控制ACC层流冷却工艺;再结晶区轧制结束温度在1000℃~1050℃之间;钢板待温厚度按3.5~4.5倍成品钢板厚度设定;非再结晶区轧制开始温度在900℃~950℃之间,其结束温度在830℃~860℃之间。钢板轧制后快速进入ACC层流冷却装置进行冷却;钢板入水温度按800℃~820℃控制,终冷温度按450℃~500℃控制,冷速按25℃/S~35℃/S进行设定。
力学性能、微观组织及抗HIC性能检验:拉伸性能及冲击韧性测试分别在WE-30万能试验机及JB-30/15冲击试验机上进行;使用光学显微镜OM扫描电镜SEM观察微观组织;根据NACETM0284-2003标准试验方法,A液:5%NaCl+0.5%CH3COOH+去离子水+H2S气体,对轧制板材试样进行HIC检验。
通过以上工艺流程,所生产的一种低锰高铬抗HIC管线用针状铁素体钢,力学性能稳定,组织均匀,具有较好的强度、塑性及一定的冲击韧性,并具有优良的抗HIC性能。其中,510MPa≤Rt0.5(屈服强度)≤600MPa、620MPa≤Rm(抗拉强度)≤800MPa、20.0%≤A50(断后伸长率)≤35.0%、100J≤-20℃-AKv(-30℃冲击功)≤230J。显微组织为针状铁素体。裂纹敏感率(CSR)≤1.0%、裂纹长度率(CLR)≤8.0%、裂纹宽度率(CTR)≤2.0%。
本发明的优点在于:通过设计合适的成分体系,在低C、低Mn成分基础上,适当提高Cr,并加入一定量微合金元素Nb、Ti等,通过严格控轧控冷工艺,稳定生产25mm及以下规格抗HIC管线用钢。通过降低Mn含量,放宽对杂质元素S和P的限制,对炼钢工序要求降低,对生产过程有利。在本专利成分体系基础上,通过简单的控轧控冷工艺,获得微观组织-针状铁素体,钢板强度及韧性匹配较好,组织均匀,为优良抗HIC性能获得提供基础。
附图说明
图1为实施例1钢板金相组织OM。
图2为实施例1钢板金相组织SEM。
具体实施方式
实施例1
根据一种低锰高铬抗HIC管线用针状铁素体钢的化学成分范围要求,完成钢水冶炼、钢坯浇铸及钢板轧制;钢坯尺寸:300mm厚*1620mm宽*3000mm长钢板尺寸:19.3mm厚*1848mm宽*12050mm长,3定尺。化学成分百分比如表1所示:
表1实施例实际化学成(%)
C | Si | Mn | Cr | Nb | Ti | P | S | Alt | N | Ca |
0.038 | 0.33 | 0.35 | 0.85 | 0.06 | 0.016 | 0.011 | 0.0067 | 0.034 | 0.0055 | 0.0030 |
1、参考液相线温度1521℃:转炉出钢1655℃;LF结束1638℃;RH结束1589℃;软吹结束温度1562℃;中包温度1538℃。
2、300mm厚连铸坯连铸过程:拉速:0.78m/min,铸坯低倍中心偏析C类0.5级。
3、采用步进梁式加热炉将钢坯加热至均热温度1170℃~1215℃,300mm厚规格钢坯在炉加热时间310min。
采用再结晶区及非再结晶区两阶段轧制及控制ACC层流冷却工艺;再结晶区轧制结束温度1025℃;钢板待温厚度77mm:非再结晶区轧制开始温度940℃,结束温度845℃;钢板入水温度按802℃,终冷温度按485℃,冷速为31℃/S。力学性能见表2所示,抗HIC性能检验结果见表3所示。
表2实施例力学性能
表3实施例HIC性能(%)
断面编号 | CLR | CTR | CSR |
1 | 6.13% | 5.31% | 0.325% |
2 | 0 | 0 | 0 |
3 | 0 | 0 | 0 |
平均值 | 2.04% | 1.77% | 0.108% |
Claims (7)
1.一种低锰高铬抗HIC管线用针状铁素体钢,其化学成分重量百分比为,C:0.03%~0.05%;Si:0.30%~0.50%;Mn:0.30%~0.50%;Cr:0.50%~1.20%;Alt:0.015%~0.050%;Nb:0.050%~0.080%;Ti:0.010%~0.020%;Ca:0.0020%~0.0040%;P:≤0.012%;S:≤0.0080%;N:≤0.0060%,其余为Fe及不可避免杂质。
2.根据权利要求1所述的铁素体钢,其特征在于,其中510MPa≤Rt0.5≤600MPa、620MPa≤Rm≤800MPa、20.0%≤A50≤35.0%、100J≤-20℃-AKv≤230J;裂纹敏感率≤1.0%、裂纹长度率≤8.0%、裂纹宽度率≤2.0%。
3.一种权利要求1所述的铁素体钢的制造方法,其特征在于,具体步骤及参数如下:
1)钢水冶炼过程中温度控制参数如下:参考液相线温度1521℃;转炉出钢1650±20℃;LF结束1635±10℃,第一炉1650±10℃;RH结束1585±5℃,第一炉1595±10℃;软吹结束温度1565±5℃;中包温度1540±5℃;
2)冶炼:采用底吹氩A模式,转炉吹炼初期底吹氩气流量设定为400m3/h、吹炼末期底吹氩气流量设定为500m3/h;
3)转炉出钢:出钢1/3时,随钢流加入白灰2.4kg~2.6kg/吨钢水、萤石0.045kg~0.055kg/吨钢水进行渣洗;出钢完毕后在渣面加铝篦子0.025kg~0.035kg/吨钢水,铝篦子拆开加入,确保铝篦子与渣反应;
4)LF炉精炼:精炼过程用低碳锰铁调Mn,处理过程禁止用铝铁脱氧及调铝,使用铝粒调铝,LF结束铝按照0.040%~0.050%控制,LF炉总调铝量不超过5kg/吨钢水,出LF炉前加入钛铁调Ti,参考吸收率80%~85%;
5)RH真空处理:提升Ar流量800~1200NL/min,进行钢水脱氢,保证深真空处理时间≥12min,最后一批合金调整完成之后,要求真空处理时间≥5min,期间测温、取样、微调成份;真空结束进行定氢;每炉钢水喂入350米SiCa线及200米Ca线,并保证钢水中Ca含量在25~30ppm之间,根据钢中钙含量调整;吊包前对钢水进行软吹,软吹氩气流量控制在≤100L/min,渣面不得翻开,保证钢水软吹时间≥12min;软吹后钢水镇静时间≥5min;
6)连铸过程,300mm厚连铸坯:拉速范围:0.75m/min~0.85m/min;动态轻压下技术;
7)钢坯加热:采用步进梁式加热炉将钢坯加热至设定均热温度1160℃~1220℃,钢坯在炉时间260min~360min,保证钢坯充分奥氏体化;
8)钢板控轧控冷:采用再结晶区及非再结晶区两阶段轧制,控制ACC层流冷却工艺;再结晶区轧制结束温度在1000℃~1050℃之间;钢板待温厚度按3.5~4.5倍成品钢板厚度设定;非再结晶区轧制开始温度在900℃~950℃之间,其结束温度在830℃~860℃之间;钢板轧制后快速进入ACC层流冷却装置进行冷却;钢板入水温度按800℃~820℃控制,终冷温度按450℃~500℃控制,冷速按25℃/S~35℃/S进行设定。
4.根据权利要求3所述的制造方法,其特征在于,步骤4)中所述的低碳锰铁,其中C:0.20wt%~0.70wt%;Mn:80.0wt%~90.0wt%;其余为杂质S、P。
5.根据权利要求3所述的制造方法,其特征在于,所述的步骤6)中连铸坯拉速为0.80m/min。
6.根据权利要求3所述的制造方法,其特征在于,所述的步骤6)中铸坯低倍中心偏析≤C类1.0级。
7.根据权利要求3所述的制造方法,其特征在于,所述的步骤7)中300mm厚规格钢坯在炉加热时间320min。
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