CN111749972B - 驱动轴及其制造方法 - Google Patents
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Abstract
本发明提供一种驱动轴及其制造方法。驱动轴(10)通过在由中碳钢构成的中空管体(12)的两端上,接合由中碳钢构成的实心短轴(14)而构成。在此,在用粒度级号表示中空管体(12)与实心短轴(14)的接合部的晶粒度时,中空管体(12)侧为#5~#9,实心短轴(14)侧为#10~#12。由此,能得到接合强度优异的驱动轴。
Description
技术领域
本发明涉及一种驱动轴及其制造方法,所述驱动轴用于在机动车中将行驶驱动力产生机构所产生的行驶驱动力向车轮传递。
背景技术
要求机动车的驱动轴既轻量,又使设置有等速万向节(Constant VelocityUniversal Joints)等的端部的刚性优异。为了对应该需求,实施了以下的一种技术方案,将轴部制成中空管体,且制成实心短轴,并且将该轴部与实心短轴进行接合(例如,参照日本发明专利公报特开2008-087003号)。作为接合方法,采用例如摩擦压接。
发明内容
中空管体的壁厚为外径与内径之差,而相对于此,实心短轴的壁厚为直径。由此可知,中空管体与实心短轴彼此的壁厚差较大。若对这样的壁厚差较大的接合件实施淬火,则有可能产生淬裂。
另外,若以确保实心短轴的硬化层深度的方式来设定淬火条件,则使中空管体的晶粒粗大化而强度下降。为了避免该情况,也可以考虑不对中空管体实施淬火。然而,在该情况下,为了使中空管体具有充分的强度,必须增大外径或壁厚。如上所述,在接合中空管体与实心短轴而得到驱动轴的情况下,明显存在难以在实现轻量化的同时确保充分的强度的问题。
本发明的一般目的在于,提供一种由中空管体与实心短轴接合而构成的驱动轴。
本发明的主要目的在于,提供一种在实现轻量化的同时表现出充分的强度的驱动轴。
本发明的另一目的在于,提供一种得到上述的驱动轴的驱动轴的制造方法。
根据本发明的一实施方式,提供一种驱动轴,其在由中碳钢构成的中空管体的两端上,接合由中碳钢构成的实心短轴而成,其特征在于,
在用粒度级号表示所述中空管体与所述实心短轴的接合部的晶粒度时,所述中空管体侧为#5~#9,且所述实心短轴侧为#10~#12。
另外,根据本发明的另一实施方式,提供一种驱动轴的制造方法,在由中碳钢构成的中空管体的两端上,接合由中碳钢构成的实心短轴,从而得到驱动轴,其特征在于,包括以下工序:
通过冷锻来得到所述实心短轴的工序;
通过摩擦压接来接合所述中空管体与所述实心短轴,在用粒度级号表示所述中空管体与所述实心短轴的接合部的晶粒度时,使所述中空管体侧为#5~#9,使所述实心短轴侧为#10~#12的工序。
根据本发明,设定中空管体与实心短轴接合的接合部的晶粒度,使中空管体侧为#5~#9,使实心短轴侧为#10~#12。通过使接合部的晶粒以这种方式细微化,能得到接合强度优异的驱动轴。另外,以这种方式得到的驱动轴还具有优异的扭转强度、疲劳强度。
而且,在该情况下,由于中空管体为中空体,因此能够实现驱动轴的轻量化。
通过参照附图对以下实施方式所做的说明,上述的目的、特征及优点应易于被理解。
附图说明
图1是本发明的实施方式所涉及的驱动轴的沿着长度方向的局部剖视侧视图。
图2是表示中空管体与实心短轴的接合部附近的显微镜照片。
图3是所述接合部附近的显微镜照片。
图4是图3中由C1所示部分的主要部分放大照片。
图5是图3中由C2所示部分的主要部分放大照片。
图6是本发明的实施方式所涉及的驱动轴的制造方法的概略流程图。
图7是表示在相同条件下,对一般的中碳钢(比较例)和满足规定组分的中碳钢(实施例1~3)进行高频淬火后的深度与C标尺(scale)的洛氏硬度(HRC)的关系的曲线图。
图8是实施例1~3的中碳钢的组分比。
图9是表示使用实施例2的中碳钢和比较例的中碳钢进行静载破坏试验的结果的曲线图。
图10是表示使用实施例2的中碳钢和比较例的中碳钢进行疲劳强度试验的结果的曲线图。
具体实施方式
下面,在本发明所涉及的驱动轴与其制造方法的关系方面,列举优选的实施方式,参照附图对本发明所涉及的驱动轴详细地进行说明。
图1是本实施方式所涉及的驱动轴10的沿着长度方向的局部剖视侧视图。该驱动轴10具有中空管体12和被设置于该中空管体12的两端部的实心短轴14。
在本实施方式中,中空管体12由中碳钢构成。作为该中碳钢的优选例,可列举出:以重量比例计,含有0.43~0.47%的C、0.20%以下的Si、0.60~0.90%的Mn、0.010%以下的P、0.008~0.020%的S、0.1%以下的Cu、0.1%以下的Ni、0.05%以下的Cr、至少0.05%以下的Mo、0.01~0.03%的Nb、0.01~0.05%的Ti中的任一种、0.02~0.04%的Al,剩余部分为Fe和不可避免的杂质。另外,该中碳钢的晶粒度用粒度级号表示为#4~#9。
实心短轴14也由中碳钢构成。作为该中碳钢的优选例,可列举出:以重量比例计,含有0.45~0.51%的C、0.25%以下的Si、0.30~0.50%的Mn、0.015%以下的P、0.008~0.020%的S、0.2%以下的Cu、0.1%以下的Ni、0.1~0.2%的Cr、至少0.05~0.25%的Mo、0.03~0.08%的Nb、0.01~0.05%的Ti中的任一种、0.02~0.04%的Al、10~30ppm的B,剩余部分为Fe和不可避免的杂质。
即,在作为实心短轴14的原材料的中碳钢中,比作为中空管体12的原材料的中碳钢含有更多的Mo、Nb、Ti。另外,构成实心短轴14的中碳钢的晶粒度用粒度级号表示为#9~#11。
图2是表示中空管体12与实心短轴14的接合部附近的显微镜照片。此外,图2中的虚线表示接合界面。中空管体12与实心短轴14的接合通过后述的摩擦压接来进行,根据图2可知,中空管体12的一部分嵌入(卷入)实心短轴14而变形。
优选中空管体12的嵌合部位的厚度(嵌入量)为1~30μm。若嵌入量小于1μm,则有可能使接合强度不充分。另一方面,若嵌入量大于30μm,则有可能在中空管体12上产生裂纹而断裂。中空管体12的优选嵌入量为15μm左右。
图3是接合部附近的显微镜照片。而且,将图3中由C1、C2所示部分的主要部分放大照片分别在图4、图5中示出。此外,图4和图5中的边框表示晶粒间界。用粒度级号表示根据显微镜照片的倍率和边框的尺寸所求得的中空管体12、实心短轴14各自的晶粒度的结果,为#5~#9、#10~#12。据此,实心短轴14和中空管体12的双方在接合部附近的晶粒均细微化。
若对晶粒的晶界附近进行分析,则发现存在作为析出粒子的Mo2C、NbC、TiC。据此,推测出Mo2C、NbC、TiC抑制晶粒的生长。另外,Mo2C、NbC、TiC阻碍作为脆性体的Fe3C的生成,由此使晶粒间界的强度提高。因此,若对驱动轴10进行拉伸试验,则中空管体12断裂而不是接合部断裂。
接着,根据图6所示的概略流程图来说明本实施方式所涉及的驱动轴10的制造方法。该制造方法包括:得到实心短轴14的短轴制造工序S1、接合中空管体12与实心短轴14的接合工序S2、退火工序S3和淬火工序S4。
如上所述,作为用于得到实心短轴14的原材料优选为中碳钢,以重量比例计,含有0.45~0.51%的C、0.25%以下的Si、0.30~0.50%的Mn、0.015%以下的P、0.008~0.020%的S、0.2%以下的Cu、0.1%以下的Ni、0.1~0.2%的Cr、至少0.05~0.25%的Mo、0.03~0.08%的Nb、0.01~0.05%的Ti中的任一种、0.02~0.04%的Al、10~30ppm的B,剩余部分为Fe和不可避免的杂质。此外,该中碳钢的晶粒度用粒度级号表示为#9~#11。
对由上述这样的组分比的中碳钢构成的钢材,在850℃以下的温度下实施轧制加工。通过在这样的温度区域下的轧制,在钢材中残留应变。另外,引起从奥氏体向铁素体的转变,并且从残留应变的凹凸析出铁素体。作为以上的结果,晶粒细微且形成易于成型加工的软质组织。
之后,对钢材实施球化退火。此时,例如可以在720~760℃下保持规定时间,然后以0.5℃/分钟以下的冷却速度进行缓冷至600℃。据此,进行渗碳体(Fe3C)的球化,形成大量存在相对软质的铁素体的组织。
接着,在短轴制造工序S1中,对球化退火后的钢材实施冷锻。通过冷锻能够避免使晶粒粗大化。换言之,晶粒在冷锻的前后被保持为微细的状态。而且,由于钢材软质,因此即使冷锻也易于成型为实心短轴14的形状。
接着,进行接合工序S2。此时,将实心短轴14或中空管体12的一方保持于保持件且使其旋转,并且对保持剩余一方的保持件施加推力,进行使两部件压接的摩擦压接。此外,以使接合时的表面温度到达800~870℃的方式,设定旋转速度、推力等条件。
如上所述,作为中空管体12的原材料的中碳钢优选为,以重量比例计,含有0.43~0.47%的C、0.20%以下的Si、0.60~0.90%的Mn、0.010%以下的P、0.008~0.020%的S、0.1%以下的Cu、0.1%以下的Ni、0.05%以下的Cr、至少0.05%以下的Mo、0.01~0.03%的Nb、0.01~0.05%的Ti中的任一种、0.02~0.04%的Al,剩余部分为Fe和不可避免的杂质。此外,该中碳钢的晶粒度用粒度级号表示为#4~#9。
如上所述,若对由这样的中碳钢构成的中空管体12通过摩擦压接接合如上述那样含Mo、Nb、Ti的实心短轴14,则在晶粒间界析出Mo2C、NbC、TiC中的至少一种。据此阻碍生成Fe3C,从而提高了晶粒间界的强度。
接着,进行退火工序S3。即,将驱动轴10加热至规定的温度。通过该退火,去除在摩擦压接时所产生的应变,并且促进再结晶化。晶粒通过再结晶而成为20μm左右的微细组织。另外,通过退火,也在晶粒间界析出NbC、VC、Mo2C等。通过以上的晶粒的细微化和在晶粒间界析出的碳化物,在接合部显现出优异的强度。此外,优选退火的温度为650~720℃,保持时间为30~90分钟。
接着,对驱动轴10进行用于进行整形的规定的机械加工,之后进行淬火工序S4。此时,优选进行高频淬火。这是由于高频淬火具有热效率优异等各种优点的原因。
在本实施方式中,能够对整个驱动轴10实施淬火。在此,由如上所述的组分的中碳钢构成的实心短轴14相比除此以外的中碳钢,更容易进行淬火。若列举具体例进行说明,则图7是在相同条件下,对一般的中碳钢(比较例)和满足上述的组分的中碳钢(实施例1~3)进行高频淬火后的C标尺的洛氏硬度(HRC)的测定结果。此外,横轴为深度,纵轴为HRC。另外,实施例1~3的具体的组分比在图8中示出。在此,图8中的“Sol-”表示固溶体。
如图7所示,示出实施例1~3的中碳钢均比作为比较例的现有技术的中碳钢的硬度高。由此可知,在实施例1~3中,相比现有技术淬火更容易进行,形成了充分的硬化层。
因此,在本实施方式中,在于中空管体12上形成充分深度的硬化层的条件下,即使实施淬火,也能确保实心短轴14的硬化层深度。如上所述,这是由于作为实心短轴14的原材料的中碳钢的淬火性优异的原因。即,避免在实施淬火的中空管体12的组织中的晶粒粗大化。因此,通过淬火,能够避免晶粒粗大化且提高中空管体12的强度。
因此,不需要增大外径或壁厚而不对中空管体12实施淬火来确保强度。相应地,能够实现驱动轴10的轻量化。另外,由于中空管体12不会被暴露于过度的加热处理中,因此避免在驱动轴10产生淬裂。
而且,在该驱动轴10中,接合部的晶粒微细,且在晶粒间界析出碳化物。通过该碳化物,获得所谓的粒子分散增强效果。根据以上这样的原因,使接合部具有优异的强度、韧性。
而且,在图9中示出使用所述实施例2的中碳钢和所述比较例的中碳钢进行静载破坏试验的结果的曲线图。另外,图10是使用所述实施例2的中碳钢和所述比较例的中碳钢进行疲劳强度试验的结果。根据该图9和图10可知,实施例2的中碳钢相比现有技术,示出优异的剪切应力、疲劳强度。即,实心短轴14示出优异的剪切应力、疲劳强度。
因此,若对驱动轴10进行拉伸试验,则中空管体12断裂而不是接合部断裂。
另外,由于中空管体12轻量,因此能够实现驱动轴10的轻量化。即,在本实施方式中,即使为中空管体12与实心短轴14接合而成的驱动轴10,也能够实现轻量化且确保充分的强度。
本发明并不特别限定于上述的实施方式,在不脱离本发明的主旨的范围内,能够进行各种变更。
Claims (5)
1.一种驱动轴的制造方法,在由中碳钢构成的中空管体(12)的两端上,接合由中碳钢构成的实心短轴(14),从而得到驱动轴(10),其特征在于,包括以下工序:
通过冷锻来得到所述实心短轴的工序;
通过摩擦压接来接合所述中空管体与所述实心短轴,在用粒度级号表示所述中空管体与所述实心短轴的接合部的晶粒度时,使所述中空管体侧为#5~#9,使所述实心短轴侧为#10~#12的工序。
2.根据权利要求1所述的驱动轴的制造方法,其特征在于,
在所述摩擦压接中,使彼此相对旋转的中空管体与实心短轴接触,通过推力施加装置施加推力,利用使所述实心短轴与所述中空管体相对压接而产生的摩擦热,使所述中空管体和所述实心短轴软化,然后,进一步施加推力,从而使所述中空管体与所述实心短轴产生固相接合。
3.根据权利要求1所述的驱动轴的制造方法,其特征在于,
使用作为所述实心短轴的原材料的中碳钢为,以重量比例计,含有C:0.45~0.51%、Si:0.25%以下、Mn:0.30~0.50%、P:0.015%以下、S:0.008~0.020%、Cu:0.2%以下、Ni:0.1%以下、Cr:0.1~0.2%、Al:0.02~0.04%和B:10~30ppm,并且,含有Mo:0.05~0.25%、Nb:0.03~0.08%、Ti:0.01~0.05%三者中的至少任一种,剩余部分为Fe和不可避免的杂质,粒度级号为#9~#11。
4.根据权利要求3所述的驱动轴的制造方法,其特征在于,
在摩擦压接的接合后,具有在保持温度650~720℃、保持时间30~90分钟的条件下,对驱动轴实施退火的工序和对退火后的驱动轴实施淬火的工序,
使所述实心短轴的金属组织中的晶粒间界析出NbC、Mo2C、TiC。
5.根据权利要求1所述的驱动轴的制造方法,其特征在于,
使用作为所述中空管体的原材料的中碳钢为,以重量比例计,含有C:0.43~0.47%、Si:0.20%以下、Mn:0.60~0.90%、P:0.010%以下、S:0.008~0.020%、Cu:0.1%以下、Ni:0.1%以下、Cr:0.05%以下和Al:0.02~0.04%,并且,含有Mo:0.05%以下、Nb:0.01~0.03%、Ti:0.01~0.05%三者中的至少任一种,剩余部分为Fe和不可避免的杂质,粒度级号为#4~#9。
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