CN1143006C - 烧结链轮及其制造方法 - Google Patents
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Abstract
本发明提供了无需锻造工序便能提高齿面抗承载性的烧结链轮。对这样的铁基烧结合金进行滚轧加工并随后进行浸碳淬火,即所述铁基烧结合金含有C、Mo、Ni,其中C的重量百分比为0.2%-0.5%,Mo的重量百分比为0.2%-1.0%、Ni的重量百分比为0.2%-1.0%,其内部基层含有铁素体和贝氏体并且它表现出铁素体与空位相邻的金属组织。
Description
发明领域
本发明涉及一种适用于例如汽车的凸轮轴定时链用链轮等的烧结链轮及其制造方法。
背景技术
作为上述链轮地知道了这样的链轮,即在例如通过锻造使链轮粗加工成形后,通过机加工精加工出形状,随后实施浸碳淬火。在这种链轮中,虽然齿面精度和齿面抗承载性出色,但存在以下缺点,即由于进行锻造工序,因此制造成本较高。另外,还知道有这样一种链轮,即通过冲压机冲裁板材并进行浸碳淬火而得到的廉价链轮。这种链轮虽然齿面抗承载性足够强,但却存在这样的问题,即因进行冲压断面的机加工,所以制造成本不仅没有降低,而且冲压加工所造成的变形还降低了齿面精度。还知道了在烧结材料定尺后实施浸碳淬火的链轮。这种链轮虽然在齿面精度及制造成本方面是出色的,但却存在齿面抗承载性恶化的问题。
如上所述,过去链轮各有利弊,因此人们迫切需要一种齿面抗承载性、齿面精度及制造成本均出色的链轮。
在用烧结材料制造链轮时出现了问题(如上所述地是齿面抗承载性问题),所述齿面抗承载性因不可避免地存在于材料内部的空位而降低。因此,为提高齿面抗承载性而应首先考虑的是提高密度,因此可考虑采用以下方法。首先,在煅烧粉末压实体后,进行定尺精压加工。接着,对煅烧材料进行冲压成形,在真正烧结后进行定尺精压加工。之后,通过进行两次当时的冲压成形和定尺精压加工,能够提高链轮密度。但是,即使采用所述的多工序制造方法,密度的提高也是有限的,不能说齿面齿面抗承载性是足够高的。另外,虽然通过锻造烧结材料而提高了密度并提高齿面抗承载性,但仍存在制造成本增大的与上述相同的问题。
因此,本发明的目的在于提供无需成本较高的锻造工序便能提高齿面抗承载性的烧结链轮及其制造方法。
发明内容
本发明的烧结链轮的特征在于,它由含有C、Mo、Ni的铁基烧结合金构成,其中C的重量百分比为0.2%-0.5%,Mo的重量百分比为0.2%-1.0%、Ni的重量百分比为0.2%-1.0%,其内部基层含有铁素体和贝氏体并且它表现出铁素体与空位相邻的金属组织。
就具有上述结构的烧结链轮来说,由于铁素体与空位相邻,因此,通过在齿面进行滚轧加工等塑性加工,使铁素体产生塑性变形并破坏齿面内侧的空位。因此,由于空位的体积减小且齿面附近的密度提高,所以在保持利用粉末冶金法的高精度齿面和低制造成本的同时,能够提高齿面抗承载性。另外,由于在内部基层中含有贝氏体,因此增强了基体强度和硬度。
为获得上述金属组成而必需上述成分。下面,对限定上述成分的理由进行说明。另外,在以下的说明中,“%”为“重量百分比”。
C:0.2%-0.5%
如果碳含量不足0.2%,则由于形成较少贝氏体,所以基体强度及硬度不够高。另外,若碳含量超过0.5%,则由于铁素体不够多,因此在对齿面进行塑性加工时的密度提高变得不充分。由这个观点出发,希望基层的铁素体按面积比地至少有40%。
Mo,Ni:0.2%-1.0%
Ni及Mo在强化基层基体的同时,也提高了淬火性,从而有助于贝氏体的生成。若Ni及Mo的含量分别不足0.2%,则其效果不充分。另一方面,若Ni及Mo的含量分别超过1%,则易于析出马氏体,以至强度降低。另外,在本发明中,不排除贝氏体和马氏体共存的情况。
基层铁素体最好按面积比地至少有40%,由此能够进一步增大滚轧加工后的密度,从而提高齿面抗承载性。另外,最好在基层外侧的最表层部上具有碳化物层,由此能够提高耐磨损性。所述碳化物层是通过浸碳处理形成的。
本发明的烧结链轮的制造方法的特征在于,对铁基烧结合金进行滚轧加工并随后进行浸碳淬火,其中所述铁基烧结合金含有C、Mo、Ni,C的重量百分比为0.2%-0.5%,Mo的重量百分比为0.2%-1.0%、Ni的重量百分比为0.2%-1.0%,其内部基层含有铁素体和贝氏体并且它表现出铁素体与空位相邻的金属组织,其中所述滚轧加工量为0.09mm-0.15mm。
附图简介
图1(A)、1(B)是表示本发明烧结链轮的金属组织的照片,(C)是表示过去烧结链轮的金属组织的照片。
图2(A)是表示滚轧加工后的链轮表面部的金属组织的照片,(B)是表示链轮烧结后的金属组织的照片,(C)是表示再次烧结后的金属组织的照片。
图3是表示滚轧加工装置的照片。
图4是表示同本发明链轮表面的距离和密度之间关系的图表。
图5是表示本发明链轮中的铁素体率与密度之间关系的图表。
图6是表示本发明链轮中的铁素体率与齿面抗承载极限之间关系的图表。
图7是表示本发明链轮中石墨添加量与铁素体率之间关系的图表。
图8是表示本发明链轮的滚轧加工量与密度之间关系的图表。
实施本发明的最佳形式
图1(A)-1(C)是表示链轮烧结后的基层金属组织的照片。如图1(A)及1(B)所示,在碳的重量百分比为0.3%-0.4%的情况下,铁素体(图中白色部分)与空位(图中黑色部分)相邻。另外,贝氏体(图中的细线掺杂部分)存在于基层中。如图1(C)所示,若碳的重量百分比为0.6%,则贝氏体增加而铁素体减少。如下所述地推定形成图1(A)及1(B)中的金属组织的理由。
即,在烧结粉末压实体时,石墨粉附近的铁粉的碳浓度局部增加,由此铁粉熔点降低并最先熔化,其会与石墨粉一起浸入颗粒间隙,从而在石墨颗粒所在处形成空位。而且,在石墨侵入之处,碳会扩散至铁粉(铁素体)内,由于在该处的碳含量增加,所以在冷却后会析出贝氏体。另一方面,可以推断出,原来与石墨粉相邻的铁粉或其中一部分在未受到碳扩散时仍以铁素体形式残存着。但这完全是推测,当然不应通过该作用的有无来限制本发明。
在上述烧结链轮的制造方法中,通过滚轧加工使链轮产生塑性变形,以此破坏空位以提高密度。另外,通过浸碳淬火引起铁原子扩散,使空位进一步收缩。因此,能够提高烧结链轮表面的密度,从而进一步提高齿面抗承载性。而且,浸碳热处理最好是在CO浓度大于1%的条件下进行的高浓度浸碳,由此能够进一步提高齿面抗承载性。
图2(A)是表示滚轧加工后的链轮表面部的金属组织的照片,从图2(A)中能够较理想地判断出压迫空位的状态。图2(B)是表示在滚轧加工后在900℃下进行浸碳淬火的链轮表面部的金属组织,与图2(A)中的金属组织相比,可以判断出,通过浸碳淬火能够几乎完全堵塞了细长空位的中央部。图2(C)是表示代替浸碳淬火在1130℃下进行再次烧结的链轮金属组织的照片,其与浸碳淬火无太大的差别,仍然几乎完全堵塞了细长空位的中央部。由此可判断出,通过温度低于再烧结的浸碳淬火,能够充分使组织变得致密。
并且,在本发明的烧结链轮的制造方法中,基层中的铁素体最好那面积比地至少有40%。另外,滚轧加工量最好为0.09mm-0.15mm,由此可以使表面部的密度达到最大限度。
实施例
下面,参照本发明的实施例对本发明作更详细的说明。
将由体积比为0.5%的Ni粉、体积比为0.5%的Mo粉、体积比为0.3%-0.6%的石墨粉、余量为铁粉所组成的粉末制成链轮,在1150℃±20℃的大气中烧结60分钟。接着,利用图3所示的滚轧加工装置,以0.09mm的滚轧加工量对链轮进行滚轧加工。图中标号1为链轮,2为冲模,在冲模2的外周面上形成与链轮相等的齿。随后,在两个冲模之间插入链轮1,通过使冲模2转动来压缩链轮齿面,从而形成按照规定的齿形。并且,滚轧加工量是指沿与链轮齿面正交的方向的压下量。在表1中给出了各链轮的石墨添加量(体积%)、碳含量(重量%)、成形密度、表面硬度、基体硬度以及铁素体的面积率。另外,分别设定同表面的距离地测定各链轮滚轧加工后的密度。其结果如表2和表1所示。
表1
石墨添加量 | 密度 | 外观硬度 | 基体硬度 HV0.1 | 铁素体面积 | 碳量 | ||
质量% | g/cm3 | HRB | 平均 | 最小 | 最大 | % | 重量% |
0.3 | 7.05 | 51 | 151 | 139 | 172 | 50 | 0.23 |
0.4 | 7.04 | 58 | 197 | 164 | 229 | 39 | 0.32 |
0.5 | 7.06 | 71 | 204 | 179 | 223 | 20 | 0.41 |
0.6 | 7.07 | 74 | 218 | 208 | 228 | 17 | 0.48 |
表2
石墨添加量 | 滚轧加工后的密度 | |||
重量% | 0.2 | 0.4 | 0.6 | 0.8 |
0.3 | 7.65 | 7.52 | 7.29 | |
0.4 | 7.42 | 7.36 | 7.12 | 7.06 |
0.5 | 7.21 | 7.2 | 7.1 | 7.05 |
0.6 | 7.21 | 7.16 | 7.03 | 7.03 |
如由图4中判断出的那样,若通过滚轧加工增加密度,则铁素体的面积率(铁素体率)增大,那么经较大程度的滚轧加工后的密度提高。这是因为与空位邻接的铁素体产生塑性变形并从而破坏空位。图5表示铁素体率和在同表面相距0.2mm部分处的密度之间的关系。从该图可判断出,若铁素体率至少为40%,则表层部能获得至少为7.5g/cm3的密度。
接着,对上述链轮进行浸碳淬火。浸碳淬火是在将链轮保持在CO浓度为0.8%的900℃气氛中60分钟的常规浸碳以及使CO浓度升至1.2%而进行的高浓度浸碳的两种条件下进行的。接着,调节各链轮密度与齿面抗承载极限之间的关系,其结果如图6所示。此处,齿面抗承载极限为将在链轮齿面上施加压力以产生变形时的压力代入赫兹公式中获得的值,以称为凹痕或压曲的疲劳破坏表示产生的齿面抗承载性。即在齿面抗承载极限下使用时,就意味着会产生凹痕或压曲,齿面抗承载极限越大,所述齿面抗承载性越好。凹痕为链轮齿面剥落的疲劳破坏,压曲为齿面凹入的疲劳破坏。如图6所示,随着链轮密度的提高,齿面抗承载极限也会提高。另外,如图6所示,若密度为7.5g/cm3或更高,则齿面抗承载极限会急剧增加。特别是,在本实施例的链轮中,由于密度最大为7.8g/cm3,因此在实施了常规浸碳淬火的链轮中,齿面抗承载极限会达到180kgf/mm2,而在实施了高浓度浸碳淬火的链轮中,齿面抗承载极限会达到220kgf/mm2。
如上所述,若铁素体率至少为40%,那么密度则会达到7.5g/cm3以上,从而齿面抗承载极限大幅度增加。在图7中示出了石墨添加量与铁素体率的关系。如图7所示,若石墨粉添加量(体积%)不大于0.38%,则铁素体率至少为4 0%。因此,希望石墨粉末添加量按体积百分比地不大于0.38%。石墨粉添加量的体积百分比最好不大于0.3%,由此能够使铁素体率至少为50%。
下面,图8示出了链轮滚轧加工量与密度之间的关系。如图8所示,链轮表面密度在滚轧加工量为0.09mm-0.15mm时达到最大。另外,即使滚轧加工量超过0.15mm,也不希望密度增加超过图8所示的最大值,另外,还可以确定的是,因冲模负荷较高,使用寿命会降低。
如上所述,本发明能够获得的效果是,由于内部基层含有铁素体和贝氏体并且表现出铁素体与空位相邻的金属组织,因此无需使用成本高的锻造工序,就能提高齿面抗承载性。
Claims (5)
1.一种烧结链轮,其特征在于:它由含有C、Mo、Ni的铁基烧结合金构成,其中碳的重量百分比为0.2%-0.5%,Mo的重量百分比为0.2%-1.0%、Ni的重量百分比为0.2%-1.0%,其内部基层含有铁素体和贝氏体并且它显示出铁素体与空位相邻的金属组织。
2.根据权利要求1所述的烧结链轮,其特征在于:所述基层的铁素体按面积比地至少有40%。
3.根据权利要求1或2所述的烧结链轮,其特征在于:在所述基层外侧的最表层部上有碳化物层。
4.一种烧结链轮的制造方法,其特征在于:对这样的铁基烧结合金进行滚轧加工并随后进行浸碳淬火,即所述铁基烧结合金含有C、Mo、Ni,其中碳的重量百分比为0.2%-0.5%,Mo的重量百分比为0.2%-1.0%、Ni的重量百分比为0.2%-1.0%,其内部基层含有铁素体和贝氏体并且它表现出铁素体与空位相邻的金属组织,其中,所述滚轧加工量为0.09mm-0.15mm。
5.根据权利要求4所述的烧结链轮的制造方法,其特征在于:所述基层的铁素体按面积比地至少有40%。
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JP2000326149A JP3698409B2 (ja) | 2000-10-25 | 2000-10-25 | 焼結スプロケット |
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EP (1) | EP1344840B1 (zh) |
JP (1) | JP3698409B2 (zh) |
CN (1) | CN1143006C (zh) |
BR (1) | BR0107374B1 (zh) |
CA (1) | CA2390254C (zh) |
DE (1) | DE60116760T2 (zh) |
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US7160351B2 (en) * | 2002-10-01 | 2007-01-09 | Pmg Ohio Corp. | Powder metal clutch races for one-way clutches and method of manufacture |
JP2005344126A (ja) * | 2002-10-04 | 2005-12-15 | Hitachi Powdered Metals Co Ltd | 焼結歯車 |
WO2005001150A1 (ja) * | 2003-06-27 | 2005-01-06 | Mitsubishi Materials Corporation | 表面緻密性および表面硬度の高い鉄基焼結合金およびその製造方法 |
JP4570066B2 (ja) | 2003-07-22 | 2010-10-27 | 日産自動車株式会社 | サイレントチェーン用焼結スプロケットの製造方法 |
JP4301507B2 (ja) * | 2003-07-22 | 2009-07-22 | 日産自動車株式会社 | サイレントチェーン用焼結スプロケットおよびその製造方法 |
US7025928B2 (en) * | 2003-07-24 | 2006-04-11 | The Gates Corporation | Method of flow forming a metal part |
JP4213060B2 (ja) * | 2004-03-03 | 2009-01-21 | 日本ピストンリング株式会社 | バルブシート用鉄基焼結合金材 |
JP2007071302A (ja) * | 2005-09-07 | 2007-03-22 | Tsubakimoto Chain Co | 突起を有する焼結製スプロケット |
JP6010015B2 (ja) | 2012-12-28 | 2016-10-19 | 株式会社神戸製鋼所 | 浸炭焼入れ材の製造方法 |
CN105215273B (zh) * | 2014-05-27 | 2017-07-11 | 遵义然泰科技有限公司 | 一种凸轮的制备方法 |
JP2016172931A (ja) * | 2016-05-12 | 2016-09-29 | Ntn株式会社 | 機械部品およびその製造方法 |
CN109930089A (zh) * | 2017-12-17 | 2019-06-25 | 宜兴安纳西智能机械设备有限公司 | 一种电池输送装置用链轮材料 |
CN109930092A (zh) * | 2017-12-17 | 2019-06-25 | 宜兴安纳西智能机械设备有限公司 | 一种电池输送装置用链轮隔套材料 |
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US3897618A (en) * | 1972-03-27 | 1975-08-05 | Int Nickel Co | Powder metallurgy forging |
US4049429A (en) * | 1973-03-29 | 1977-09-20 | The International Nickel Company, Inc. | Ferritic alloys of low flow stress for P/M forgings |
US4954171A (en) * | 1987-09-30 | 1990-09-04 | Kawasaki Steel Corp. | Composite alloy steel powder and sintered alloy steel |
JP2648519B2 (ja) * | 1989-10-03 | 1997-09-03 | 日立粉末冶金株式会社 | シンクロナイザーハブの製造方法 |
EP0600421B1 (en) * | 1992-11-30 | 1997-10-08 | Sumitomo Electric Industries, Limited | Low alloy sintered steel and method of preparing the same |
DE19521941C1 (de) * | 1995-06-07 | 1996-10-02 | Mannesmann Ag | Verfahren und Vorrichtung zur Herstellung von Sinterteilen |
JPH09157806A (ja) | 1995-12-04 | 1997-06-17 | Mitsubishi Materials Corp | 高強度鉄基焼結合金 |
CA2240426C (en) * | 1995-12-15 | 2005-05-10 | Zenith Sintered Products, Inc. | Duplex sprocket/gear construction and method of making same |
JP2000510907A (ja) * | 1996-05-13 | 2000-08-22 | ザ プレスメット コーポレーション | 高性能鉄系材料の製造方法 |
US5729822A (en) * | 1996-05-24 | 1998-03-17 | Stackpole Limited | Gears |
US5997805A (en) * | 1997-06-19 | 1999-12-07 | Stackpole Limited | High carbon, high density forming |
JPH11124603A (ja) * | 1997-10-21 | 1999-05-11 | Jatco Corp | 焼結金属合金、該焼結金属合金の製造方法及び該焼結金属合金を用いた焼結合金歯車 |
WO2000062960A1 (fr) * | 1999-04-16 | 2000-10-26 | Unisia Jecs Corporation | Materiau de moulage a base de poudre metallique et corps moule par recompression, corps fritte obtenu a partir dudit corps moule par recompression, et procedes de production y relatifs |
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EP1344840A1 (en) | 2003-09-17 |
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EP1344840B1 (en) | 2006-01-18 |
BR0107374A (pt) | 2002-09-24 |
JP2002129295A (ja) | 2002-05-09 |
DE60116760D1 (de) | 2006-04-06 |
DE60116760T2 (de) | 2006-07-13 |
CA2390254C (en) | 2005-08-02 |
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CN1394238A (zh) | 2003-01-29 |
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US6670048B2 (en) | 2003-12-30 |
BR0107374B1 (pt) | 2009-01-13 |
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