CN1084392C - 耐热开裂和耐磨性提高的热轧用轧辊 - Google Patents

耐热开裂和耐磨性提高的热轧用轧辊 Download PDF

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CN1084392C
CN1084392C CN97114701A CN97114701A CN1084392C CN 1084392 C CN1084392 C CN 1084392C CN 97114701 A CN97114701 A CN 97114701A CN 97114701 A CN97114701 A CN 97114701A CN 1084392 C CN1084392 C CN 1084392C
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C·J·马德鲁德
T·埃里桑
U·费舍尔
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Abstract

根据本发明，提供了一种含70～95wt%，优选地85～94%的WC、粘结相只含钴或者是一种含20～35wt%的Ni、最高10%的Cr及可能少量添加的钼的Co-Ni-Cr合金的热轧用轧辊。WC晶粒是圆形的，其平均粒径在3～10μm之间，优选地4～8μm，最大粒径不超出平均值的两倍，组织中小于平均粒径值一半的晶粒不大于2%。

Description

耐热开裂和耐磨性提高的热轧用轧辊
本发明涉及热轧钢丝和钢条用的胶结碳化物轧辊。这些轧辊是用含WC及由Co或者一种Co+Ni或Co+Ni+Cr的合金构成的粘结相的胶结碳化物品牌制成的。
与铸铁、钢或高速钢制成的轧辊相比，用胶结碳化物制成的热轧用轧辊的表面温度低。这将推迟热裂纹的产生并降低在轧槽中的磨蚀磨损，(轧槽是轧辊与热坯相接触时轧辊的槽状部分)。它也将减少轧辊经热循环产生的疲劳。总之，这常使轧槽的寿命比用其他材料制成的轧辊的寿命多10-20倍，并已导致广泛利用胶结碳化物轧辊热轧丝、条和异形材。
胶结碳化物的热导率与粘结相的含量成反比，这是因为碳化钨比粘结相的热导率高。当增大粘结相含量时由于减少了碳化物/碳化物界面区，故在粘结相内发生更多的热传递。
当为一定的热轧用途选择组成时常遇到一个问题即平衡两种需求：抵抗机械应力的坚韧材料和把粘结相含量降至最低以使材料具有尽可能高的热导率从而抵抗热裂纹的形成和热疲劳，并在不增加由于机械过载造成的裂纹的危险下得到尽可能长的轧槽寿命。
由送进轧辊的热坯的冷端造成的许多冲击和高分离力导致高的机械应力，它导致所用的品牌应具有从600到1250HV3范围内的硬度和从10到30％重量百分比的钴含量。为了保持这样低的硬度值，必须尽可能使用粗晶品牌，必须能在不增加硬度下减少粘结相含量，从而降低了材料的韧性。
胶结碳化物是通过粉末冶金方法制备的，包括湿磨含有能形成硬质成分的粉末和粘结相粉末的粉末混合物，把碾磨的混合物干燥成为具有良好流动性的粉末，把干燥后的粉末压制成所需形状的块体，并最后烧结。
高强度的碾磨过程是在不同尺寸的碾磨机中用胶结碳化物碾磨体进行的。据认为为了在碾磨过的混合物中得到均匀分布的粘结相，碾磨是必要的。据认为高强度的碾磨能使混合物产生活性，该活性在烧结过程中进一步促进了致密结构的形成，碾磨时间在几小时到几天的数量级。
用碾磨粉末制备的材料在烧结后的显微结构的特征在于，尖锐的有棱角的WC晶粒具有相当宽的WC粒径分布，常含有相当大的晶粒，它是由于烧结过程中细晶粒的溶解、再结晶和晶粒长大而造成的。
美国专利5505902和5529804公开了制备胶结碳化物的方法，根据这些方法基本排除了碾磨，为了在粉末混合物中得到均匀分布的粘结相，而是对硬质成分晶粒用粘结相进行预涂覆，该混合物进一步与压制剂混合、压制成型并烧结。在所述的第一个专利中涂覆是用溶胶-凝胶法进行的，在第二个专利中，是用多元醇。在使用这些方法时由于不存在烧结过程中晶粒长大，故有可能保持与烧结前同样的晶粒尺寸和形状。
图1是1200X下根据原有技术制备的胶结碳化物轧辊的显微结构照片
图2是1200X下根据本发明的胶结碳化物轧辊的显微结构照片
图3是根据原有技术制备的胶结碳化物轧辊的照片，表明了使用一段时间后轧槽的磨损图案。
图4是根据本发明制备了胶结碳化物轧辊的照片，表明了使用同样时间后轧槽的磨损图案。
现已令人意外地发现用上述美国专利的工艺制备的胶结碳化物具有改善的机械、热和疲劳性能，结果使热轧用轧辊的性能得到提高。在最终所得材料中，WC骨架的邻接度(Contiguity)比用磨碾粉末制备的具有相同粘结相含量和相同硬度的材料的值高，它们之间唯一的区别是由于碾磨粉末在烧结过程中有显著的再结晶和晶粒长大而造成的结构的不同，烧结过程中的不同行为使材料得到更高的WC骨架的邻接度，导致材料有更高的热导率。由于材料产生了更连续和刚性的WC骨架，故也可预计它有更高的强度。更窄的粒径分布和由于可控烧结过程造成的不存在很粗的WC晶粒，也导致材料对裂纹的产生和扩展有更好的抵抗性。
根据本发明，提供了一种热轧用轧辊，它含有70～95wt％，优选地85～94％的WC；粘结相只有钴或者是一种含20～35wt％的Ni，最高10wt％的Cr和可能添加的最高5wt％的钼的Co-Ni-Cr合金；WC晶粒是圆形的，平均粒径在3～10μm之间，优选地4-8μm；最大粒径不超出平均值的两倍，结构中小于平均粒径值一半的晶粒不大于2％。
在一个优选实施例中，组成应含有约87％的WC和含32wt％的Ni和8wt％的Cr的Co基粘结相，WC的平均粒径为4.5μm，邻接度C应大于0.5，C值由线性分析确定： C = 2 · N WC / WC 2 · N WC / WC + N WC / binder
式中NWC/WC是每单位长度的参考线上碳化物/碳化物晶界数量，NWC/binder是碳化物/粘结相的晶界数量。
根据本发明的方法，热轧用轧辊的制备工艺为，通过带或不带筛分的喷射碾磨将WC粉末碾磨成已除去了粗晶粒和细晶粒并具有窄粒径分布的粉末。然后用Co根据上述美国专利之一对该WC粉末进行涂覆，小心地把该WC粉末与能形成粘结相以达到预期最终组成的粉末及压制剂一起湿法混合成浆料。另外，为了避免粗WC晶粒的沉降，根据瑞典专利申请9702154-7添加增稠剂，混合的方式应能在不碾磨的情况下得到均匀的混合物，即不出现粒径的减小。用喷雾干燥法对浆料进行干燥，根据标准工艺用喷雾干燥后的粉末压制轧辊并进行烧结。
实施例1
制施备了两组直径158mm、宽65mm的热轧用胶结碳化物轧辊。胶结碳化物中含有平均粒径为4.5μm的WC和13％的组成为60wt％Co、32wt％Ni和8wt％Cr的粘结相。两种材料的硬度为约100Hv3。
方案A：WC、Co、Ni和Cr的粉末按预期组成的数量进行碾磨、干燥、压制和烧结。轧辊具有根据图1的显微结构。
方案B：WC粉末经喷射研磨并被分离成2～9μm的粒径范围，然后用美国专利5505902中公开的方法用Co涂覆该粉末使WC粉末含有约2wt％的钴。该粉末小心地与为得到预期最终组成的Co、Ni和Cr粉末和压制剂一起在不碾磨情况下混合，干燥后该粉末经压制并烧结得到一种根据图2的显微结构。
测定两种方案的邻接度得到下述结果：
方案             邻接度
A：原有技术       0.43
B：根据本发明     0.53
用这两种方案的试条测定横断裂强度得到下述结果：
方案            横断裂强度MPa    标准偏差％
A：原有技术            1950          5.5
B：根据本发明          2250          3.3
显然，与用原有技术制备的具有同样组成和硬度的材料相比，根据本发明制备的材料有更高的横断裂强度，这表明与用正常碾磨途径制备的材料相比，这种材料具有更窄的性能。
在一个滚轧机上运行该轧辊，轧制最终直径为5.6mm的不锈钢丝(主要为品牌AISI 316L)，轧辊有椭圆形的轧槽，并安装在轧纲丝机的第一台，这里坯料速率为约40m/s，缩减量为20％，在该台上热坯的表面温度为约950℃。
结果：
方案A：1200吨后，轧槽有严重的热裂纹图案(见图3)并被重新磨去0.6mm的厚度以去除所有裂纹。
方案B：1200吨后没观察到热裂纹图案(见图4)，只看到正常的磨损。1800吨后轧槽有轻微的热裂纹图案，被重新磨掉0.4mm。

Claims (6)

1、一种含70～95wt％WC、粘结相只含钴或者是一种含20～35wt％的Ni、最高10％的Cr的Co-Ni-Cr合金的热轧用轧辊，其特征在于WC晶粒是圆形的，其平均粒径在3～10μm之间，并且最大粒径不超出平均值的两倍，组织中小于平均粒径值一半的晶粒不大于2％。
2、根据权利要求1的热轧用轧辊，其中所述WC的含量为85-94％，WC晶粒的平均粒径在4-8μm之间。
3、根据权利要求1的热轧用轧辊，其中所述Co-Ni-Cr合金还添加了少量钼，所述WC晶粒平均粒径为4-8μm。
4、根据前述权利要求1的热轧用轧辊，其特征在于其组成含有约87％的平均粒径为4.5μm的WC和含32wt％Ni和8wt％Cr的Co基粘结相，该组成的邻接度C＞0.5，C值由线性分析测定，即 C = 2 · N WC / WC 2 · N WC / WC + N WC / binder
式中Nwc/wc是每单位长度的参考线上碳化物/碳化物晶界数量，NWC/binder是碳化物/粘结相的晶界数量。
5、一种含70～95％的平均粒径在3～10μm之间的WC的热轧用轧辊的制备方法，其特征在于，通过带或不带筛分的喷射碾磨将WC粉末碾磨成已除去粗晶粒和细晶粒的窄粒径分布的粉末，把该WC粉末与能形成粘结相以得到预期最终组成的粉末、压制剂和增稠剂在不碾磨条件下、即不发生粒径减少条件下、一起湿法混合成浆料，用喷雾干燥法干燥浆料，根据标准工艺用喷雾干燥粉末压制轧辊并烧结。
6、根据前述权利要求5的方法，其特征在于在混合之前用钴涂覆WC粉末。
CN97114701A 1996-07-19 1997-07-18 耐热开裂和耐磨性提高的热轧用轧辊 Expired - Fee Related CN1084392C (zh)

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SE518810C2 (sv) * 1996-07-19 2002-11-26 Sandvik Ab Hårdmetallkropp med förbättrade högtemperatur- och termomekaniska egenskaper
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DE69707581T2 (de) 2002-05-16
ZA976040B (en) 1998-02-02
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JPH1080706A (ja) 1998-03-31
DE69707581D1 (de) 2001-11-29
US5902942A (en) 1999-05-11
EP0819490A1 (en) 1998-01-21
SE9602810D0 (sv) 1996-07-19
ATE207396T1 (de) 2001-11-15
SE517473C2 (sv) 2002-06-11
CN1171985A (zh) 1998-02-04
EP0819490B1 (en) 2001-10-24

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