CN114951663A - 高速钢丝材的制备方法 - Google Patents
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Abstract
本发明涉及粉末冶金技术领域,公开了一种高速钢丝材的制备方法,在熔炼母合金的过程中,加入的RE‑M中间合金占RE‑M总重量的40~60%;将母合金一边电渣,一边加入剩余La‑M和Yb‑M中间合金;并在电渣重熔后不经过凝固和再次熔化的步骤而直接雾化制成合金粉末;在制粉过程中,同时喷射0.5~2μm的TiC或/和VN粉末,得到TiC或/和VN粉末复合的合金粉末;将合金粉末制备成棒料;对棒料烧结和分级热处理、变形前退火处理,然后再对粉末块体坯料进行变形处理得丝材后再次分级热处理。本发明制备的粉末高速钢纯净度更高,非金属夹杂物和有害气体含量减少90%,强度明显提升。
Description
技术领域
本发明涉及粉末冶金技术领域,特别涉及一种高速钢丝材的制备方法。
背景技术
高速钢具有高硬度、高强度、耐磨性好的特点,广泛应用于精密刀具制作以及模具制造业。相比于传统的铸造高速钢,利用粉末冶金法制备得到的高速钢显著地改善了显微组织当中碳化物偏析的问题,极大地提升了材料的力学性能以及工作时的稳定性。目前商用的粉末冶金高速钢主要由气雾化合金粉-热等静压联合法进行制备,得到的高速钢具有明显的细晶组织,碳化物均匀分布,强度性能均在3500MPa以上,部分牌号性能可以达到4000MPa以上,但是由于生产所耗成本居高不下,严重限制了其大规模应用。有研究报道,利用商业M2合金粉掺杂氮化钒粉末通过球磨活化与冷压烧结的方式,在1160℃可以基本实现材料的致密化,相对密度高达99.4%,强度性能也能够维持在2500~3000MPa左右,并极大地降低了生产成本。因此,本发明旨在公开一种冷压烧结法制备低成本、高性能的粉末冶金高速钢的方法。
发明内容
发明目的:针对高速钢材料寿命低的问题,本发明提供一种高速钢丝材的制备方法,制备的高速钢组织细小、碳化物均匀、有害杂质量少,抗弯强度、韧性和耐磨性明显提升。
技术方案:本发明提供了一种高速钢丝材的制备方法,S1:按配比取用原料Fe、W、Mo、Co、V、Nb的纯金属或中间合金以及C-Fe、Si-Fe、Mn-Fe、Cr-Fe、RE-M中间合金,并对所有原料进行干燥处理,采用真空感应熔炼技术熔炼母合金;在熔炼母合金的过程中,加入的RE-M中间合金占RE-M总重量的40~60%;S2:电渣重熔雾化:将S1制备的母合金电渣重熔,一边电渣,一边加入剩余La-M和Yb-M中间合金;并在电渣重熔后不经过凝固和再次熔化的步骤而直接雾化制成合金粉末;在所述制粉过程中,同时喷射0.5~2μm的TiC或/和VN粉末,得到TiC或/和VN粉末复合的合金粉末; S3:对合金粉末依次进行球磨、还原退火、粉末压坯,制备成直径为10~200mm的棒料;S4:对S3所得棒料进行烧结;S5:对S4所得烧结后的棒料进行分级热处理;S6:先对所述S5所得粉末块体坯料进行变形前退火处理,然后再对粉末块体坯料进行锻造和/或挤压、轧制、拉拔处理,在变形量达到5~30%时,再次进行所述变形前退火处理,然后再次对所述粉末块体坯料进行锻造和/或挤压、轧制、拉拔处理;所述变形前退火处理与所述锻造和/或挤压、轧制、拉拔处理交替进行,直至最终得到φ1-3mm的丝材;S7:对S6所得丝材再次进行分级热处理。
优选地,在所述S1中,熔炼母合金的具体工艺如下:在真空度10-5~103Pa的条件下,首先在1380~1580℃熔化Fe、W、Mo、Co、V、Nb纯金属,保温10~15min,然后在1280~1580ºC加入C-Fe、Si-Fe、Mn-Fe、Cr-Fe的中间合金,搅拌均匀后除渣,保温15~35min,然后在1250~1450ºC加入40~50%的RE-M中间合金,搅拌均匀,保温3~5min,出炉前电磁搅拌3~5min。
进一步地,在所述S2中,雾化制成合金粉末的方式为气雾化制粉,采用氩气雾化,氩气纯度99.9%,雾化压力10~30MPa,制备出来的合金粉末的D50为20~60μm。
优选地,在所述S3中,所述球磨的具体工艺如下:将S2制备的合金粉末与硬脂酸锌放入太空杯中,放入钢球,钢球与混合粉末的体积比约为3~5:1;钢球采用直径 4mm、6mm、8mm三种不同大小,比例为1:1:2;将太空杯置于一维滚筒式混料机上,混料机转速约为40~60转/分,混料时间30~72小时。
进一步地,在所述S3中,所述还原退火的工艺如下:在真空炉内进行,炉内成真空状态或惰性气体保护状态,将粉末平铺在基板上,厚度为5~10mm,多层基板叠加放置,相邻基板间距30~100mm,温度400~680℃,保温时间60~300min,随炉冷却到室温后取出。过程中检测炉内气氛氧含量,使氧含量小于10ppm。
进一步地,在所述S3中,所述粉末压坯的工艺为非HIP压坯:将经还原退火后的合金粉末称重后放入压坯模具中,将粉末双向模压制成块体坯料;压力500~1200MPa。
优选地,在所述S4中,所述烧结的方式为常压保护性气氛烧结:(1)烧结炉内冲入保护性惰性气体,排出氧气,使烧结炉内的氧含量小于1ppm;(2)以6~10℃/min的速度升温至650~850℃,保温时间t=3~5min/cm×d,;(3)以8~10℃/min的速度升温至1180~1260℃,保温时间t=10~30min/cm×d;(4)随炉冷却至室温;其中,d为样品的最大壁厚,单位cm。
进一步地,在所述S5和/或S7中,所述分级热处理的工艺如下: (1)预热:以5~10℃/min的升温速度加热至580~620℃,保温时间t=3~5min/cm×d;(2)二次预热:紧接着以5~10℃/min的升温速度加热至840~860℃,保温时间t=2~4min/cm×d;(3)淬火保温:紧接着以5~10℃/min的升温速度加热至1170~1260℃,保温时间t=2~4min/cm×d;(4)淬火冷却:紧接着,当d≥10时,首先以103~105℃/s的降温速度降温至300~500℃,保温时间t=0.1~1.5min/cm×d,然后以103~105℃/s的降温速度降温至20~40℃,保温时间t=0.1~1.5min/cm×d;当10≥d≥5时,以103~105℃/s的降温速度降温至200~400℃,保温时间t=0.1~1.5min/cm×d,然后以103~105℃/s的降温速度降温至20~40℃,保温时间t=0.1~1.5min/cm×d;当d≤5cm时,以103~105℃/s的降温速度降温至20~40℃,保温时间t=0.1~1.5min/cm×d;(5)深冷处理:紧接着以105~107℃/s的降温速度降温至-50~-150℃,保温时间t=1~2min/cm×d;(6)回火:紧接着以5~10℃/min的升温速度加热至560~570℃,保温时间t=1~3h/cm×d;(7)冷却:紧接着随炉冷却至200~300℃,出炉空冷至20~40℃;(8)重复(6)和(7)至少一次;其中,d为样品的最大壁厚,单位cm。粉末高速钢由于其特殊性,热处理工艺也区别与一般的金属,主要区别是需要预热、淬火温度较高和回火温度高且回火次数多;变形以后的粉末高速钢棒料内应力较大、硬度很高,因此必须首先进行退火。退火温度为840~880℃,退火时间t=2~20min/cm×d。高速钢中合金元素含量较多,导热性差,加热前必须进行预热,预热温度依次为580~620℃和840~880℃,预热时间t=2~5min/cm×d。淬火温度为1170~1260℃,淬火后水冷或油冷至室温。最后,560~570℃回火三次,每次保温时间t=1~3h×d。高速钢回火必须注意以下四点:(1)淬火后必须及时回火,否则会使奥氏体稳定化,不利于消除残余奥氏体(一般不超过8h),(2)回火温度力求均匀,最好在盐浴炉或带风扇井式回火炉中进行,力求加热均匀,(3)每次回火后必须冷至室温,才能重复以后的各次回火,(4)回火后必须冷至室温方可清洗,否则易变形开裂。此条件下制备出的粉末高速钢晶粒和第二相细化均匀,细小而弥散的颗粒状碳化物分布在回火马氏体基上。未闭合的孔隙呈圆形或者椭圆形。硬度达到67.5HRC,红硬性达到63.2HRC,抗弯强度可达4146.3MPa。优选地,在所述S6中,所述变形前退火处理的工艺如下:将粉末块体坯料在真空炉或盐浴炉中以≤2.5℃/min的升温速率加热到850~870℃,保温110~130min后,以≤400℃/h的升温速率升温至1100~1300℃,保温15~30min,接着降温至850~870摄氏度,保温60~120min,然后在炉中以10~30℃/h的降温速率降温至500~600℃,然后空冷或随炉冷却到200℃左右后出炉空冷至室温。
有益效果:(1)本发明中,将电渣和制粉同时进行,并且在制粉过程中加入TiC极细粉,优势在于:①使得电渣后的母合金纯净度更高,不会因再次熔化而造成二次污染;②TiC极细粉为雾化熔滴提供异质形核的核心,促进晶粒趋于极细的球形形态,细化基体组织和碳化物,有利于力学性能的提升;③在组分中引入稳定的TiC颗粒,为烧结过程细化晶粒、均匀化组分提供重要的作用;④粉末的纯净度更高,与普通方法相比,非金属夹杂物和有害气体含量减少90%。
(2)本发明中,组分中加入RE稀土元素,主要是去除组分中的杂质元素氧。由于RE元素的化学性质非常活泼,几乎可以还原所有的金属氧化物,生成性质稳定的RE-O氧化物,不仅可以净化组分,减少有害元素O的危害,而且形成的RE-O氧化物还可以作为异质形核的核心,增大异质形核率,细化晶粒,提高强韧性。并且,在真空熔炼和电渣精炼阶段分别加入RE-M的中间合金,目的是提高RE-M的利用率,防止真空熔炼阶段全部加入时烧损过于严重,不能确保充分地除去熔体中的氧,最终使熔体更加纯净。
(3)粉末复合雾化后的粉末,TiC粉末不熔化,为凝固提供大量的非均匀形核的核心,促进异质形核,起到细化晶粒和碳化物尺寸作用,有利于提高材料的硬度、耐磨性和抗弯强度等力学性能。随后通过球磨工艺消除粉末中的孔隙和不均分布的成分,优化合金的成分和组织,为优异的性能奠定基础。
附图说明
图1为分级热处理的工艺图(d≥10或10≥d≥5时);
图2为分级热处理的工艺图(d≤5cm时);
图3为变形前退火处理的工艺图。
具体实施方式
下面结合附图对本发明进行详细的介绍。
实施例1:
本实施方式提供了一种高速钢丝材的制备方法,包括以下步骤:S1:按配比取用原料Fe、W、Mo、Co、V、Nb的纯金属以及C-Fe、Si-Fe、Mn-Fe、Cr-Fe、RE-M中间合金,并对所有原料进行干燥处理,采用真空感应熔炼技术熔炼母合金;在熔炼母合金的过程中,加入的RE-M中间合金占RE-M总重量的50%;
上述熔炼母合金的具体工艺如下:在真空度10-1Pa的条件下,首先在1540℃熔化Fe、W、Mo、Co、V、Nb纯金属,保温15min,然后在1480ºC加入C-Fe、Si-Fe、Mn-Fe、Cr-Fe的中间合金,搅拌均匀后除渣,保温15min,然后在1350ºC加入45%的RE-M中间合金,搅拌均匀,保温5min,出炉前电磁搅拌3min。
上述原料形态为:纯金属、RE-M中间合金为铸锭料,其余中间合金C-Fe、Si-Fe、Mn-Fe、Cr-Fe、La-M、Yb-M、V-N或Nb-N、Ti-C为粉末料压制成的颗粒料;加料顺序为先加铸锭料,后加粉末料。
S2:电渣重熔雾化:将S1制备的母合金电渣重熔,一边电渣,一边加入剩余La-Fe和Yb-Fe中间合金;并在电渣重熔后不经过凝固和再次熔化的步骤而直接雾化制成合金粉末;在所述制粉过程中,同时喷射0.5~2μm的TiC和VN粉末,得到TiC和VN粉末复合的合金粉末;
在上述电渣重熔的同时,通过加强结晶器出料口的冷却能力(用冷却水或直接将坯料一端拉入水中)、保温熔池侧壁的方法(线圈加热+传感器)控制熔池的温度梯度,使凝固方向与熔池侧壁的夹角保持20~30°,得到净化后的母合金熔体。
上述雾化制成合金粉末的方式为气雾化制粉,采用氩气雾化,氩气纯度99.9%,雾化压力10MPa,制备出来的合金粉末的D50为20μm。
S3:对合金粉末依次进行球磨、还原退火、粉末压坯,制备成直径为200mm的棒料;
上述球磨的工艺为:
具体地说:将S2制备的合金粉末与硬脂酸锌放入太空杯中,放入钢球,钢球与混合粉末的体积比约为3:1;钢球采用直径 4mm、6mm、8mm三种不同大小,比例为1:1:2;将太空杯置于一维滚筒式混料机上,混料机转速约为40转/分,混料时间30小时。
上述还原退火的工艺如下:
在真空炉内进行,炉内成真空状态或惰性气体保护状态,将粉末平铺在基板上,厚度为5mm,多层基板叠加放置,相邻基板间距30mm,温度400℃,保温时间60min,随炉冷却到室温后取出。过程中检测炉内气氛氧含量,使氧含量小于10ppm。
上述粉末压坯的工艺为非HIP压坯:将经还原退火后的合金粉末称重后放入压坯模具中,将粉末双向模压制成块体坯料;压力1200MPa。
S4:对S3所得棒料进行烧结;
上述烧结的方式可以为常压保护性气氛烧结:(1)烧结炉内冲入保护性惰性气体,排出氧气,使烧结炉内的氧含量小于1ppm;(2)以10℃/min的速度升温至650℃,保温时间t=5min/cm×d,;(3)以10℃/min的速度升温至1220℃,保温时间t=20min/cm×d;(4)随炉冷却至室温;其中,d为样品的最大壁厚,单位cm。
S5:对S4所得烧结后的棒料进行分级热处理;
上述分级热处理的工艺如下(如图1和2):
(1)预热:以5℃/min的升温速度加热至580℃,保温时间t=3min/cm×d;
(2)二次预热:紧接着以5℃/min的升温速度加热至840℃,保温时间t=2min/cm×d;
(3)淬火保温:紧接着以5℃/min的升温速度加热至1170℃,保温时间t=2min/cm×d;
(4)淬火冷却:紧接着,
当d≥10时,首先以104℃/s的降温速度降温至300℃,保温时间t=1min/cm×d,然后以104℃/s的降温速度降温至20℃,保温时间t=1.5min/cm×d(如图1);
当10≥d≥5时,以105℃/s的降温速度降温至200℃,保温时间t=1min/cm×d,然后以104℃/s的降温速度降温至40℃,保温时间t=1.5min/cm×d(如图1);
当d≤5cm时,以105℃/s的降温速度降温至40℃,保温时间t=1.5min/cm×d(如图2);
(5)深冷处理:紧接着以105℃/s的降温速度降温至-100℃,保温时间t=1min/cm×d;
(6)回火:紧接着以5℃/min的升温速度加热至560℃,保温时间t=1h/cm×d;
(7)冷却:紧接着随炉冷却至200℃,出炉空冷至40℃;
(8)重复(6)和(7)至少一次;
其中,d为样品的最大壁厚,单位cm。
S6:先对所述S5所得粉末块体坯料进行变形前退火处理,然后再对粉末块体坯料进行锻造和/或挤压、轧制、拉拔处理,在变形量达到12%时,再次进行所述变形前退火处理,然后再次对所述粉末块体坯料进行锻造和/或挤压、轧制、拉拔处理;所述变形前退火处理与所述锻造和/或挤压、轧制、拉拔处理交替进行,直至最终得到φ3mm的丝材;
上述变形前退火处理的工艺如下(如图3):
将棒料在真空炉或盐浴炉中以2.5℃/min的升温速率加热到850℃,保温130min后,以400℃/h的升温速率升温至1250℃,保温15min,接着降温至870℃,保温100min,然后在炉中以30℃/h的降温速率降温至500℃,然后随炉冷却到200℃后出炉空冷至室温。
上述锻造的工艺如下:
预热:首先以8℃/min的加热速度将坯料加热至620℃,保温时间t=3min/cm×d ;然后以8℃/min的升温速度加热至860℃,保温时间t=2min/cm×d;其中,d为样品的最大壁厚,单位cm;
锻造:对坯料进行锻造,每次减小量为5%,每次锻造完后直接将坯料重新放入840℃的炉中加热,加热时间t=3min/cm×d,直至将坯料锻造至所需尺寸;
冷却:将锻造完成的坯料放入炉中随炉冷却至200℃,然后出炉空冷至室温。
上述挤压的方式为热挤压,工艺如下:
预热:首先以7℃/min的加热速度将坯料加热至620℃,保温时间t=5min/cm×d;然后以7℃/min的升温速度加热至900℃,保温时间t=4min/cm×d;其中,d为样品的最大壁厚,单位cm;
热挤压:挤压方式为卧式挤压,挤压速度5mm/s,单次挤压截面减小8%,挤压模具预热温度750℃;
冷却:将挤压完成的坯料放入炉中随炉冷却至260℃,然后出炉空冷至室温。
S7:对S6所得丝材再次进行分级热处理。本步骤中的分级热处理工艺如图1和2,与上述S5中的工艺相同,此处不做赘述。
实施例2:
本实施例与实施例1大致相同,不同点仅在于,本实施方式中,在步骤S1中,
原料形态为:80%铸锭料+20%粉末料压制成的颗粒料;加料顺序为先加铸锭料,后加粉末料。
除此之外,本实施例与实施例1完全相同,此处不做赘述。
实施例3:
本实施例与实施例1大致相同,不同点仅在于,本实施方式中,
S2:电渣重熔雾化:将S1制备的母合金电渣重熔,一边电渣,一边加入剩余RE-M中间合金,以喂丝方式加入;并在电渣重熔后不经过凝固和再次熔化的步骤而直接雾化制成合金粉末;在所述制粉过程中,同时喷射0.5~1.5μm的TiC和VN粉末,得到TiC和VN粉末复合的合金粉末;
S3:对合金粉末依次进行球磨、还原退火、粉末压坯和热挤压,制备成直径为200mm的棒料;
上述球磨的工艺为:
具体地说:将S2制备的高速钢粉末与硬脂酸锌放入太空杯中,放入钢球,钢球与混合粉末的体积比约为4:1;钢球采用直径 4mm、6mm、8mm三种不同大小,比例为1:1:3;将太空杯置于一维滚筒式混料机上,混料机转速约为30转/分,混料时间50小时。
除此之外,本实施例与实施例1完全相同,此处不做赘述。
对比例1:
使用“孙海霞, 陈存广, 张振威, 郭志猛, 低氧超细粉末制备高性能粉末高速钢, 稀有金属材料与工程 48(10) (2019) 3246-3251. ”中公开的配方和方法制备丝材。
通过下表1展示实施例1至3以及对比例1的方法制备得到的丝材性能。
表1
上述实施方式只为说明本发明的技术构思及特点,其目的在于让熟悉此项技术的人能够了解本发明的内容并据以实施,并不能以此限制本发明的保护范围。凡根据本发明精神实质所做的等效变换或修饰,都应涵盖在本发明的保护范围之内。
Claims (9)
1.一种高速钢丝材的制备方法,其特征在于,包括以下步骤:
S1:按配比取用原料Fe、W、Mo、Co、V、Nb的纯金属或中间合金以及C-Fe、Si-Fe、Mn-Fe、Cr-Fe、RE-M中间合金,并对所有原料进行干燥处理,采用真空感应熔炼技术熔炼母合金;在熔炼母合金的过程中,加入的RE-M中间合金占RE-M总重量的40~60%;
S2:电渣重熔雾化:将S1制备的母合金电渣重熔,一边电渣,一边加入剩余La-M和Yb-M中间合金;并在电渣重熔后不经过凝固和再次熔化的步骤而直接雾化制成合金粉末;在所述制粉过程中,同时喷射0.5~2μm的TiC或/和VN粉末,得到TiC或/和VN粉末复合的合金粉末;
S3:对合金粉末依次进行球磨、还原退火、粉末压坯,制备成直径为10~200mm的棒料;
S4:对S3所得棒料进行烧结;
S5:对S4所得烧结后的棒料进行分级热处理;
S6:先对所述S5所得粉末块体坯料进行变形前退火处理,然后再对粉末块体坯料进行锻造和/或挤压、轧制、拉拔处理,在变形量达到5~30%时,再次进行所述变形前退火处理,然后再次对所述粉末块体坯料进行锻造和/或挤压、轧制、拉拔处理;所述变形前退火处理与所述锻造和/或挤压、轧制、拉拔处理交替进行,直至最终得到φ1-3mm的丝材;
S7:对S6所得丝材再次进行分级热处理。
2.根据权利要求1所述的高速钢丝材的制备方法,其特征在于,在所述S1中,熔炼母合金的具体工艺如下:
在真空度10-5~103Pa的条件下,首先在1380~1580℃熔化Fe、W、Mo、Co、V、Nb纯金属,保温10~15min,然后在1280~1580ºC加入C-Fe、Si-Fe、Mn-Fe、Cr-Fe的中间合金,搅拌均匀后除渣,保温15~35min,然后在1250~1450ºC加入40~50%的RE-M中间合金,搅拌均匀,保温3~5min,出炉前电磁搅拌3~5min。
3.根据权利要求1所述的高速钢丝材的制备方法,其特征在于,在所述S2中,雾化制成合金粉末的方式为气雾化制粉,采用氩气雾化,氩气纯度99.9%,雾化压力10~30MPa,制备出来的合金粉末的D50为20~60μm。
4.根据权利要求2所述的高速钢丝材的制备方法,其特征在于,在所述S3中,所述球磨的具体工艺如下:
将S2制备的合金粉末与硬脂酸锌放入太空杯中,放入钢球,钢球与混合粉末的体积比约为3~5:1;钢球采用直径 4mm、6mm、8mm三种不同大小,比例为1:1:2;将太空杯置于一维滚筒式混料机上,混料机转速约为40~60转/分,混料时间30~72小时。
5.根据权利要求1所述的高速钢丝材的制备方法,其特征在于,在所述S3中,所述还原退火的工艺如下:在真空炉内进行,炉内成真空状态或惰性气体保护状态,将粉末平铺在基板上,厚度为5~10mm,多层基板叠加放置,相邻基板间距30~100mm,温度400~680℃,保温时间60~300min,随炉冷却到室温后取出;过程中检测炉内气氛氧含量,使氧含量小于10ppm。
6.根据权利要求1所述的高速钢丝材的制备方法,其特征在于,在所述S3中,所述粉末压坯的工艺为非HIP压坯:将经还原退火后的合金粉末称重后放入压坯模具中,将粉末双向模压制成块体坯料;压力500~1200MPa。
7.根据权利要求1所述的高速钢丝材的制备方法,其特征在于,在所述S4中,所述烧结的方式为常压保护性气氛烧结:(1)烧结炉内冲入保护性惰性气体,排出氧气,使烧结炉内的氧含量小于1ppm;(2)以6~10℃/min的速度升温至650~850℃,保温时间t=3~5min/cm×d,;(3)以8~10℃/min的速度升温至1180~1260℃,保温时间t=10~30min/cm×d;(4)随炉冷却至室温;
其中,d为样品的最大壁厚,单位cm。
8.根据权利要求1所述的高速钢丝材的制备方法,其特征在于,在所述S5和/或S7中,所述分级热处理的工艺如下:
(1)预热:以5~10℃/min的升温速度加热至580~620℃,保温时间t=3~5min/cm×d;
(2)二次预热:紧接着以5~10℃/min的升温速度加热至840~860℃,保温时间t=2~4min/cm×d;
(3)淬火保温:紧接着以5~10℃/min的升温速度加热至1170~1260℃,保温时间t=2~4min/cm×d;
(4)淬火冷却:紧接着,
当d≥10时,首先以103~105℃/s的降温速度降温至300~500℃,保温时间t=0.1~1.5min/cm×d,然后以103~105℃/s的降温速度降温至20~40℃,保温时间t=0.1~1.5min/cm×d;
当10≥d≥5时,以103~105℃/s的降温速度降温至200~400℃,保温时间t=0.1~1.5min/cm×d,然后以103~105℃/s的降温速度降温至20~40℃,保温时间t=0.1~1.5min/cm×d;
当d≤5cm时,以103~105℃/s的降温速度降温至20~40℃,保温时间t=0.1~1.5min/cm×d;
(5)深冷处理:紧接着以105~107℃/s的降温速度降温至-50~-150℃,保温时间t=1~2min/cm×d;
(6)回火:紧接着以5~10℃/min的升温速度加热至560~570℃,保温时间t=1~3h/cm×d;
(7)冷却:紧接着快速冷却至200~300℃,保温时间t=0.3~1h/cm×d,出炉空冷至20~40℃;
(8)重复(6)和(7)0~1次;
其中,d为样品的最大壁厚,单位cm。
9.根据权利要求1所述的高速钢丝材的制备方法,其特征在于,在所述S6中,所述变形前退火处理的工艺如下:
将粉末块体坯料在真空炉或盐浴炉中以≤2.5℃/min的升温速率加热到850~870℃,保温110~130min后,以≤400℃/h的升温速率升温至1100~1300℃,保温15~30min,接着降温至850~870摄氏度,保温60~120min,然后在炉中以10~30℃/h的降温速率降温至500~600℃,然后空冷或随炉冷却到200℃左右后出炉空冷至室温。
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