• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    The present invention relates to a method for manufacturing a nitrided low-alloy steel part comprising the following steps: a) decarburizing the surface of a low-alloy steel part comprising at least one addition element that is both nitrurigenic and carburigenic in order to obtain a decarburized part having a carbon-depleted surface layer of thickness less than or equal to 1.5 mm, the minimum carbon content in the carbon-depleted surface layer being less than or equal to 70% of the mass content carbon in the core of the decarburized part, b) treatment of the decarburized part by quenching treatment followed by a treatment of income, and c) nitriding of the carbon-depleted surface layer in order to obtain the low-alloy steel part nitrided, step c) being performed after step b).
    公开号:FR3032723A1
    申请号:FR1551179
    申请日:2015-02-13
    公开日:2016-08-19
    发明作者:Alain Viola；Nicolas Binot
    申请人:Messier Bugatti Dowty SA；
    IPC主号:
    专利说明:

    [0001] BACKGROUND OF THE INVENTION The invention relates to a method for manufacturing nitrided low-alloy steel parts as well as to low-alloy steel parts that are decarburized and capable of undergoing nitriding treatment. The low-alloyed nitriding steels typically have a carbon content of between 0.20% and 0.45% which makes it possible to confer on the base material its mechanical properties at the core after heat treatment. The superficial properties of steel such as hardness can be conferred by a nitriding treatment which consists in diffusing ferritic phase nitrogen and which generates the precipitation of submicroscopic nitrides from nitrurigenic elements such as Cr, V, Mo and Al, present in solid solution in the treated steel. Concretely, in a nitriding treatment, the steel can be treated at a temperature of about 500 ° C by ammonia, which decomposes into cracked ammonia and reacts simultaneously with the iron of the steel. Ammonia causes the formation of a surface layer of iron nitrides, called the combination layer, from which the nitrogen atoms diffuse towards the core of the part to form the diffusion layer. For a weakly alloyed steel comprising nitrurigenic elements, two layers can be observed after nitriding: the surface combination layer consisting of iron nitrides and the diffusion layer in which the submicroscopic nitride precipitates at the origin of the nitride are dispersed. hardness increase observed in the nitrided layer.
    [0002] The depth of the nitriding layer may vary, depending on the nitriding conditions and the targeted applications, between 0.05 mm and 1 mm. The nitriding treatment, however, remains a relatively long process to implement. It would be desirable to further improve the surface properties of the nitriding layers and to reduce the duration of the nitriding treatments. There is therefore a need to improve surface properties, especially hardness, of nitriding layers formed on the surface of low alloy steel parts. There is still a need to accelerate the apparent kinetics of the nitriding treatments of low alloy steel parts, ie to reduce the time required to obtain at a given depth a significant increase in hardness, for example from minus 200 HV, relative to the hardness of the core steel. OBJECT AND SUMMARY OF THE INVENTION To this end, the invention proposes, according to a first aspect, a method of manufacturing a nitrided low alloy steel part comprising the following steps: a) decarburizing the surface of a part in low-alloy steel comprising at least one addition element both nitrurigene and carburigen to obtain a decarburized piece having a carbon-depleted surface layer of thickness less than or equal to 1.5 mm, the minimum mass content of carbon in the carbon-depleted surface layer being less than or equal to 70% of the carbon mass content in the core of the decarburized part, b) treatment of the decarburized part by a quenching treatment followed by a treatment of income, and c) nitriding the carbon depleted surface layer to obtain the nitrided low alloy steel part, step c) being performed after step b). "Low alloy steel" means a steel for which no alloying element is present in a mass content greater than 5.00%. In other words, in a low-alloy steel, each of the chemical elements, other than iron, is present in a mass content less than or equal to 5.00%.
    [0003] By "addition element both nitrurigenic and carburigenic" is meant an addition element present in the steel in the form of carbides before step c) and capable of forming during the stage c) a nitride. As an example of both nitrurigenic and carburigenic addition element, mention may be made, for example, of the following elements: Cr, Mo and V. The carbon mass content at the core of the part does not vary during step a ). In other words, the surface decarburization carried out in step a) affects the carbon content only at the level of the surface layer of the part and not at the level of the core thereof. It is possible that depending on the depth of the carbon-depleted surface layer, the carbon mass content varies. Thus, by "minimum carbon content in the carbon-depleted surface layer", it is necessary to understand the minimum value attained by the carbon mass content when moving along the depth of the carbon-depleted surface layer in parallel. at the carbon mass content gradient. The carbon mass content is measured, for example, by a Castaing microprobe in the framework established by the ASTM E1019 standard. The carbon mass content at the heart of the decarburized part (corresponding to that of the part before decarburization) may, for example, be between 0.20% and 0.45%. In the invention, the minimum mass content of carbon in the carbon-depleted surface layer is less than or equal to 70% of the carbon mass content in the core of the decarburized part. In other words, the minimum carbon content in the carbon-depleted surface layer is less than or equal to 0.70 * (carbon mass content in the core of the decarburized part). The inventors have found that the layer obtained by nitriding does not have optimal properties if carbon is present in an excessively high content in the surface layer of the part 30 before the nitriding treatment. In this case, there is a high content of carbides in the surface layer before nitriding which can be problematic. Indeed, the nitrides obtained by substitution of carbon with nitrogen in the carbides (in-situ nitride precipitation) during the nitriding treatment have a lower curing potential than the nitrides obtained by precipitation from elements 3032723 4 nitrurigenes initially present in solid solution in the ferritic matrix. In addition, during nitriding, the carbon initially present in the carbides of the surface layer can be released and diffuse upstream of the nitrogen diffusion front. This carbon thus released can precipitate in the form of cementite networks at the grain boundaries and thus alter the mechanical properties of the nitrided layer. Thus, the invention is based on the fact of performing a decarburizing treatment of the surface of the workpiece before the nitriding treatment in order to reduce the amount of carbides present on the surface of the workpiece and thus to overcome the undesirable effects of carbon previously mentioned while maintaining good properties in the heart of the room outside this superficial layer. The decarburization treatment carried out in step a) makes it possible to obtain a superficial layer of optimized chemical composition for receiving the nitriding treatment due to the elimination, after treatment of decarburization, of at least a portion of the carbides which contribute, during nitriding, to the formation of carbide / carbonitride networks detrimental to the mechanical strength of the nitriding layer. The invention advantageously makes it possible to significantly increase the surface hardness of the nitrided part and to obtain more intense compression stress fields making it possible to significantly improve the fatigue strength of the steel part thus treated. The invention makes it possible, in particular, to reduce or eliminate the quantity of weakening cementitious networks. In addition, the invention makes it possible to significantly accelerate the apparent nitriding kinetics due to the reduction in the amount of carbon at the surface of the part, thus resulting in a greater contribution of the nitrogen to the curing mechanism. Thus, with respect to the case where step a) is not carried out before the nitriding, the parts treated by the process according to the invention have, for an identical nitrogen content in the nitriding layer, a greater hardness, which apparently returns to an acceleration of the nitriding kinetics (everything happens as if more nitrogen was present at a given depth in the case of the parts treated by the method according to the invention).
    [0004] The invention can thus make it possible to rapidly obtain deep nitride layers, for example 0.7 mm deep.
    [0005] The increase in the apparent nitriding kinetics also advantageously makes it possible to limit the relaxation of the residual stresses in the nitriding layer because of the possibility of reducing the time of exposure to the nitriding temperature.
    [0006] The intermediate tempering and tempering step is, for its part, intended to confer its properties on the base steel. In an exemplary embodiment, the quenching (cooling) can be performed from the decarburization temperature and the income is then achieved. Alternatively, the decarburized part can first be cooled, for example to room temperature (20 ° C.), then austenitized and after the austenitization quenched treatment followed by a treatment of income. . In an exemplary embodiment, the minimum carbon content in the carbon-depleted surface layer may be less than or equal to 60% of the carbon mass content in the core of the decarburized part. In other words, the minimum mass content of carbon in the carbon-depleted surface layer may be less than or equal to 0.6 * (carbon mass content in the core of the decarburized part).
    [0007] Nitriding can be carried out under conventional conditions by any type of nitriding process known to those skilled in the art. The temperature and time atmosphere settings are defined based on the base steel and the desired characteristics.
    [0008] In an exemplary embodiment, the thickness of the carbon-depleted surface layer may be between 0.3 mm and 1.5 mm. In an exemplary embodiment, the minimum carbon mass content in the carbon-depleted surface layer may be greater than or equal to 0.05%. The treated low alloy steel part may, for example, be made of 32CrMoV13, 35CrMo4, 15CrMoV6 or X38CrMoV5 steel. The treated low-alloy steel part may preferably be 32CrMoV13 steel. In an exemplary embodiment, the low alloyed steel part can be treated during step a) by an oxidizing atmosphere comprising steam by imposing a temperature of between 850 ° C. and 1000 ° C. the oxidizing atmosphere having a dew point temperature between -40 ° C and + 20 ° C, for example between -10 ° C and + 10 ° C, for example between -4 ° C and + 4 ° C. Alternatively, the low alloy steel part can be treated during step a) with air at a temperature of 950 ° C. in order to achieve the desired decarburization. In an exemplary embodiment, it is possible to carry out, before step c), a step of machining the carbon-depleted surface layer. Performing such a machining step is advantageous because it can make it possible to eliminate an undesirable oxidized layer that can be formed during decarburization. This oxidized layer may typically have a thickness less than or equal to a few hundredths of a millimeter. There are other ways of reducing the amount of oxides on the surface of the decarburized part, it is thus possible, for example, to subject the decarburized part to treatment with a reducing atmosphere, for example comprising H 2, before step c). . The machining step of the carbon-depleted surface layer can be performed before and / or after step b). In an exemplary embodiment, it is possible after step 20 c) to perform a step of machining the nitriding layer formed in step c). The realization of such a machining step can make it possible to eliminate the combination layer formed during the nitriding treatment, only the diffusion layer formed during this treatment being preserved. In an exemplary embodiment, it is possible to seek to obtain a carbon-depleted surface layer after implementation of step a) in one or more predefined zones of the surface of the part. In this case, it is for example possible to coat the surface of the low-alloy steel part of a mask prior to step a) so as to carry out the decarburization only in one or more predefined zones of the surface of the part. delimited by the mask. It is thus possible, for example, to deposit an oxygen barrier varnish on the surface of the part, the zone or zones on which the varnish has not been deposited being intended to be decarburized during step a).
    [0009] It is still possible to eliminate, before step c), a portion of the carbon-depleted surface layer in order to keep it only in one or more predefined areas of the surface of the part.
    [0010] The present invention also relates to a decarburized low-alloy steel component comprising at least one addition element which is both nitrurigenic and carburigenic and which has a carbon-depleted surface layer of thickness less than or equal to 1.5 mm intended to undergo nitriding, the minimum carbon content in the carbon-depleted surface layer being less than or equal to 70% of the carbon mass content in the core of the decarburized part. Such a part corresponds to the intermediate product obtained by carrying out step a) described above before carrying out the nitriding step c).
    [0011] In an exemplary embodiment, the carbon-depleted surface layer may have a thickness of between 0.3 mm and 1.5 mm. Preferably, the low alloy steel may be 32CrMoV13 steel.
    [0012] The various characteristics described above for the process according to the invention relating to the carbon-depleted surface layer and the low-alloy steel used are applicable to the aspect relative to the part according to the invention.
    [0013] BRIEF DESCRIPTION OF THE DRAWINGS Other features and advantages of the invention will be apparent from the following description, with reference to the accompanying drawings, in which: - Figures 1 to 3 show very schematically the evolution of the surface composition of a piece of low-alloy steel during a nitriding treatment depending on whether this part has been decarburized or not, - Figures 4, 7 and 10 in particular show results obtained by microprobe of Castaing showing the evolution of the Carbon mass content in a surface decarburized part, and FIGS. 5, 6, 8, 9 and 11 are measurement results comparing the hardnesses obtained for nitrided parts according to whether they have or not. not previously subjected to surface decarburization treatment.
    [0014] DETAILED DESCRIPTION OF EMBODIMENTS FIGS. 1 to 3 show very schematically the evolution of the surface composition of a low-alloy steel part during a nitriding treatment depending on whether this part has been decarburized. ("Decarburized steel") or not ("Raw steel tempered / tempered"). In both cases, the part has on its surface on the one hand chromium in solid solution 1 as well as carbides enriched in chromium 2 called chromium carbides. The decarburized part has in its carbon-depleted surface layer 3 a smaller amount of chromium carbides 2 than the non-decarburized part. The part is, during nitriding, for example treated with a gas stream comprising ammonia. Figures 2 and 3 show schematically the evolution of the surface composition of the part during nitriding and compare it to the superficial composition of the part before nitriding. As illustrated in Figure 2, the carbides of chromium 2 are, during nitriding, converted to nitrides of chromium 4 carbides and carbon 5 is released. Chromium in solid solution 1 is, in turn, converted during nitriding chromium nitride 6 from chromium in solid solution.
    [0015] As mentioned above, chromium nitrides 4 may impart less hardness to the nitride layer than chromium nitrides 6. The nitrided layer obtained when the part has been previously decarburized therefore advantageously has a better hardness due to lower proportion of chromium nitrides 4.
    [0016] Furthermore, as illustrated in FIG. 3, if the released carbon content exceeds a certain threshold of the cementitious networks 7 may appear which can weaken the nitriding layer obtained. In the case where the decarburization was not performed prior to nitriding, a larger number of embrittling cementitious networks are formed due to a greater amount of carbon released during nitriding.
    [0017] EXAMPLES EXAMPLE 1 A 32CrMoV13 nitriding steel in the annealed state was first decarburized by treatment with an oxidizing atmosphere comprising water vapor and having a dew point of +4. ° C at a temperature of 950 ° C for 6 hours. FIG. 4 shows the evolution as a function of the depth of the carbon mass content and the hardness of the decarburized low alloy steel part thus obtained. As illustrated, such a decarburization treatment results in a carbon content of about 0.12% at the surface of the carbon-depleted surface layer (Opm depth), the carbon content of the steel base being found at a depth of about 0.85 mm. The minimum carbon content in the carbon-depleted surface layer thus obtained is about 0.08%. Following this decarburization treatment, oil quenching was carried out and then a tempering treatment was carried out at a temperature of 635 ° C. for 4 hours under an N 2 + 10% H 2 atmosphere. A second oil quench was performed after the tempering. Nitriding under an atmosphere composed of 50% NH 3, 37.5% H 2 and 12.5% N 2 at a temperature of 520 ° C for a period between 101 hours and 113 hours was performed. FIG. 5 provides the microhardness measurement results for the nitrided low alloy steel part obtained in the context of the present example ("Decarburized alloy + tempering + nitriding"). By way of comparison, FIG. 5 shows the microhardness measurements obtained when the same steel is subjected to a treatment differing only in that the decarburization is not performed ("crude" + "nitriding" alloy). It can be seen that the implementation of a process according to the invention makes it possible, by virtue of carrying out the decarburization before the nitriding, to significantly improve the surface hardness of the part obtained. The shift in the curve relating to the realization of a decarburization treatment to the right with respect to the "crude" + "nitriding" curve also shows that the apparent kinetics of nitriding is improved within the scope of the invention.
    [0018] FIG. 6 shows the evolution of the difference in hardness with respect to that of the core as a function of depth for a workpiece obtained according to example 1 or obtained under conditions identical to those of example 1. with the exception that the decarburization treatment was not performed. For the part obtained according to Example 1, it is found that a significant surface hardness gain of about 32% (637-436 / 637) is achieved. EXAMPLE 2 A type 32CrMoV13 nitriding steel in the annealed state was treated under the same conditions as in Example 1. The only difference is that the decarburization was carried out at a temperature of 980 ° C. and not more than 950 ° C. Figure 7 shows the change as a function of the depth of the carbon mass content and the hardness of the decarburized low alloy steel part thus obtained. As illustrated, such a decarburization treatment leads to the production of a carbon content of less than 0.10% on the surface of the carbon-depleted surface layer (Opm depth), the carbon content of the base steel. being found at a depth of about 0.9 mm. The carbon content at the surface of the carbon-depleted surface layer corresponds in this case to the minimum carbon content in the carbon-depleted surface layer. FIG. 8 provides the microhardness measurement results for the nitrided low alloy steel part obtained in the context of the present example ("Decarburized alloy + tempering + nitriding"). By way of comparison, FIG. 8 shows the microhardness measurements obtained when the same steel is subjected to a treatment differing only in that the decarburization is not carried out ("crude" + "nitriding" alloy). It can be seen that the implementation of a process according to the invention makes it possible, by virtue of carrying out the decarburization before the nitriding, to significantly improve the surface hardness of the part obtained. The shift in the curve relating to the realization of a decarburization treatment to the right with respect to the "crude" + "nitriding" curve also shows that the apparent kinetics of nitriding is improved within the scope of the invention.
    [0019] For its part, FIG. 9 shows the evolution of the difference in hardness with respect to that of the core as a function of depth for a part obtained according to example 2 or obtained under conditions identical to those of example 2. with the exception that the decarburization treatment was not performed. For the part obtained according to Example 2, it is found that a significant surface hardness gain of the order of 30% (627-436 / 627) is obtained. Example 3 An annealed annealed 32CrMoV13 nitriding steel was first decarburized by treatment with an oxidizing atmosphere comprising water vapor and having a dew point of 0 ° C under a temperature of 950 ° C. ° C for 6 hours. Figure 10 shows the change as a function of the depth of the carbon mass content and the hardness of the decarburized low alloy steel part thus obtained. As illustrated, such a decarburization treatment leads to a carbon content of about 0.20% at the surface of the carbon-depleted surface layer (Opm depth), the carbon content of the steel of base being found at a depth of about 0.85 mm. The minimum carbon content in the carbon-depleted surface layer thus obtained is about 0.16%. Following this decarburization treatment, oil quenching was performed and then a tempering treatment was carried out at 635 ° C for 4 hours under N2 + 10% H2 atmosphere. A second oil quench was performed after the treatment of income. Nitriding under an atmosphere composed of 50% NH 3, 37.5% H 2 and 12.5% N 2 at a temperature of 550 ° C for a period of 55 hours was performed. FIG. 11 shows the evolution of the difference in hardness with respect to that of the core as a function of the depth for a part obtained according to example 3 ("decarburized alloy + income + nitriding") or obtained under conditions identical to those of Example 3 except that the decarburization treatment was not carried out ("crude" + "nitriding" alloy). For the part obtained according to Example 3, it is found that a significant gain in surface hardness is achieved. The phrase "comprising / including a" should be understood as "comprising / including at least one". The expression "understood between ... and ..." or "from ... to" must be understood as including boundaries.
    权利要求:
    Claims (9)
    [0001]
    REVENDICATIONS1. A method of manufacturing a nitrided low-alloy steel part comprising the following steps: a) decarburizing the surface of a low-alloy steel part comprising at least one addition element at the same time nitrurigenic and carburigenic in order to obtain a decarburized part having a carbon-depleted surface layer of thickness less than or equal to 1.5 mm, the minimum carbon content in the carbon-depleted surface layer being less than or equal to 70% of the carbon content at the core of the decarburized part, b) treatment of the decarburized part by quenching treatment followed by a treatment of income, and c) nitriding of the carbon-depleted surface layer in order to obtain the nitrided low-alloy steel part, the step c) being performed after step b).
    [0002]
    2. Method according to claim 1, characterized in that the thickness of the carbon-depleted surface layer is between 0.3 mm and 1.5 mm.
    [0003]
    3. Method according to any one of claims 1 and 2, characterized in that it is carried out before step c), a machining step of the carbon-depleted surface layer.
    [0004]
    4. Method according to any one of claims 1 to 3, characterized in that is carried out after step c) a machining step of the nitriding layer formed in step c).
    [0005]
    5. Method according to any one of claims 1 to 4, characterized in that the minimum mass content of carbon in the carbon-depleted surface layer is greater than or equal to 0.05%. 3032723 14
    [0006]
    6. Method according to any one of claims 1 to 5, characterized in that the treated low-alloy steel piece is 32CrMoV13 steel. 5
    [0007]
    7. A low-alloy, decarburized steel part comprising at least one addition element that is at the same time nitrurigenic and carburigenic and has a carbon-depleted surface layer of thickness less than or equal to 1.5 mm intended to undergo nitriding, the mass content The minimum carbon content in the carbon-depleted surface layer is less than or equal to 70% of the carbon mass content in the core of the decarburized part.
    [0008]
    8. Part according to claim 7, characterized in that the carbon-depleted surface layer has a thickness of between 0.3 mm and 1.5 mm.
    [0009]
    9. Part according to any one of claims 7 and 8, characterized in that the low alloy steel is 32CrMoV13 steel. 20 25 3035
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    2016-02-23| PLFP| Fee payment|Year of fee payment: 2 |
    2016-08-19| PLSC| Publication of the preliminary search report|Effective date: 20160819 |
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    2017-06-23| CD| Change of name or company name|Owner name: MESSIER-BUGATTI-DOWTY, FR Effective date: 20170518 |
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    优先权:
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