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    • 专利摘要:
    A part for a fuel injection component is made of steel having compositions in mass% of C: 0.08 to 0.16%, of Si: 0.10 to 0.30%, of Mn: 1 0.00 to 2.00%, S: 0.005 to 0.030%, Cu: 0.01 to 0.30%, Ni: 0.40 to 1.50%, Cr: 0.50 to 1.50 %, Mo: 0.30 to 0.70%, V: 0.10 to 0.40%, s-Al: 0.001 to 0.100%, and Fe and impurities. After heating the part, the part is subjected to hot forging, then cooled in a temperature range of 800 ° C to 500 ° C and at the speed of 0.02 ° C / s to define a surface ratio of a bainitic structure after hot forging of 85% or more.Figure of the abstract: Fig. 2
    公开号:FR3082211A1
    申请号:FR1906042
    申请日:2019-06-06
    公开日:2019-12-13
    发明作者:Makoto HARITANI；Yuuki Tanaka；Tomohiro ANDOH；Kazuyoshi Kimura；Takahiro Miyazaki；Keisuke Inoue；Toshimasa Ito；Koji Morita；Tomomitsu FUKUOKA；Tadashi Nishiwaki
    申请人:Denso Corp；
    IPC主号:
    专利说明:

    Title of the invention: METHOD FOR MANUFACTURING A FUEL INJECTION COMPONENT Technical field [0001] The present disclosure relates to a method for manufacturing a fuel injection component having a high resistance to fatigue under internal pressure .
    Conventionally, heat treated steels which are quenched and returned (heat refining treatment) after hot work such as hot forging have been used for automotive components, mechanical structural components and the like, requiring strength and tenacity.
    However, although the heat treated steels are excellent in terms of strength and toughness, a concern relates to the high heat treatment costs for the quenching and tempering treatment (heat refining treatment) after hot treatment during component manufacturing. In addition, in heat treated steel, a heat treatment distortion accompanied by a martensitic transformation is important, and the amount of machining for shape correction and dimension correction after the heat treatment increases, leading to degradation in productivity. In addition, since the machining is carried out in a hard martensite state, there is concern that the machinability (processability) is low, that the time required to manufacture the component is long and that the cost is high.
    For this reason, the non-heat treated steel which develops a required hardness while being maintained in a hot working state and which can reach a desired strength even if the quenching and tempering treatment after hot working is omitted is widely used as a substitute for heat treated steel in mechanical structural components and the like as a material which can meet cost reduction.
    For example, even in fuel injection components such as a common rail, which is used in a fuel injection system to directly inject fuel under high pressure into a fuel chamber of each cylinder and to which high internal pressure is repeatedly applied, a non-heat treated steel of a ferrite-pearlite type, as disclosed in JP 5778055 B, was used.
    [0006] However, a common rail made of non-heat treated steel of the ferritic-pearlitic type has been able to withstand fuel pressure (pressure in the common rail) of up to 250 MPa, but a concern is that it is difficult to develop a high resistance (tensile strength and yield strength) corresponding to a fuel pressure of class 270 to 300 MPa, which is expected to become common in the future. There is also a risk of brittle rupture when a maximum operating pressure or an abnormally high pressure is applied.
    On the other hand, as a non-heat treated steel, there is a non-heat treated bainitic steel having a bainitic structure during its hot treatment. Although non-heat treated bainitic steel may have a higher resistance than non-heat treated ferrite-perlite steel, the toughness is still insufficient and an improvement in the fatigue characteristics under internal pressure is necessary for the application to the component. fuel injection to which a fuel pressure greater than 250 MPa is applied.
    Document IP 2012-246527 A describes a technology for a steel component for a mechanical structure with high resistance to fatigue and high toughness in which an area ratio of the bainitic structure is defined at 95% or more and the width of a bainite wafer is set to 5 µm or less by controlling a cooling rate from the final hot forging temperature to 300 ° C. It should be noted that the technology described in the document IP 2012-246527 A differs from the present disclosure in a range of temperatures and in a range of cooling rates for controlling a cooling rate. In addition, Ni is not added to an alloy composition and a specific measure to increase toughness and fatigue resistance is different from that described in the present disclosure.
    An object of the present disclosure is to provide a method of manufacturing a fuel injection component having a higher resistance to fatigue under internal pressure.
    According to one aspect of the present disclosure, a method is provided for the manufacture of a fuel injection component by treating a workpiece in a predetermined shape. The part is manufactured in a steel having compositions in mass% of C: 0.08 to 0.16%, of Si: 0.10 to 0.30%, of Mn: 1.00 to 2.00%, of S: 0.005 to 0.030%, Cu: 0.01 to 0.30%, Ni: 0.40 to 1.50%, Cr: 0.50 to 1.50%, Mo: 0.30 to 0.70%, V: 0.10 to 0.40%, s-Al: 0.001 to 0.100%, and inevitable Fe and impurities as residual components. The method includes subjecting the workpiece to hot forging after heating the workpiece to a temperature of 950 ° C or more and 1350 ° C or less. The method further includes a first cooling of the part, after hot forging, at an average cooling rate of 0.1 ° C / s or more in a temperature range from 800 ° C to 500 ° C. The method further comprises a second cooling of the part, after the first cooling, at an average cooling rate of 0.02 ° C / s or more and 10 ° C / s or less in a subsequent temperature range of 500 ° C to 300 ° C to establish an area ratio of a bainitic structure after hot forging of 85% or more. The heating temperature described above represents a temperature on the surface of the room. The average cooling rate represents an average cooling rate at the workpiece surface.
    According to the present disclosure, the steel further contains one or two of Ti: <0.100% and Nb: <0.100% by mass.
    According to another aspect of the present disclosure, a maximum diameter / area m . lx of non-metallic inclusions estimated by a statistical method of the extreme values in the part after hot forging is 300 µm or less. Non-metallic inclusions represent inclusions residing in steel and which are a sulfide containing MnS as the main component, an oxide containing ΓΑ12Ο2 as the main component and / or a nitride containing TiN as the main component.
    According to another aspect of the present disclosure, the method further comprises performing, after hot forging, an aging treatment in a temperature range from 550 ° C to 700 ° C.
    According to another aspect of the present disclosure, the method further comprises the execution of an autofrettage process on the part in which a fuel flow channel is formed.
    As described above, the present invention improves the toughness by minimizing the cementite precipitated in the bainitic structure by using a steel material (workpiece) having a high Ni content and a low C content and by controlling the average cooling speed after hot forging, thereby improving the fatigue strength under internal pressure of the fuel injection component to be manufactured.
    In non-heat treated bainitic steel, the addition of Ni is particularly effective in increasing the resistance, that is to say the value of the fracture toughness, against the propagation of cracks in the presence of a crack when a force is applied from the outside. For this reason, according to the present disclosure, Ni has a high content of 0.40% or more.
    In addition, according to the present disclosure, an average cooling speed after hot forging, more precisely, the average cooling speed in a temperature range from 500 ° C to 300 ° C is controlled to be 0, 02 ° C / s or more and 10 ° C / s or less with the reduction of the C content. As a result, the toughness is improved by minimizing the appearance of cementite, which is generated during the cooling process after forging hot and can be a starting point for the generation of cracks.
    According to the present invention, the structure after hot forging is substantially a bainitic single-phase structure. More specifically, the surface ratio of the bainitic structure is fixed at 85% or more. In fact, when the ferrite structure is mixed in the structure, not only the aging hardening characteristics are lowered, but the bearing capacity ratio and the durability ratio are also lowered, as a result of which a concern about reduction resistance to fatigue appears. For this reason, according to the present disclosure, the average cooling rate in the temperature range of 800 ° C to 500 ° C is controlled to be 0.1, 1 ° C / s or more.
    According to the present disclosure, one or two types among Ti and Nb can be included at a predetermined content if necessary.
    According to the present disclosure, it is preferable that the maximum diameter / area m . 1x non-metallic inclusions estimated by a statistical method of extreme values in the workpiece which has been subjected to hot forging is set at 300 µm or less. The internal pressure fatigue strength of the fuel injection component can be further improved by reducing the generation of coarse non-metallic inclusions which can be the starting point for generating cracks.
    In addition, according to the present disclosure, once the structure maintained to be hot forged is substantially a bainitic single-phase structure, the hardness can be increased by a subsequent aging treatment to achieve high strength. At this stage, in order to miniaturize the carbide of Mo, the carbide of V or analogs precipitated in the steel, it is preferable to carry out an aging treatment in a temperature range going from 550 ° C to 700 ° C.
    The method may include performing machining on the part.
    In particular, the method may include performing machining on the part from a fuel flow channel in the part; and performing an auto-frettage process on the part’s fuel flow channel.
    As a measure to increase the fatigue strength under internal pressure of the fuel injection component such as a common rail, an autofrettage method is known, in which an internal pressure is applied to a channel d fuel flow inside the fuel injection component to apply residual stress. In the manufacturing method according to the present disclosure, the fatigue strength under internal pressure can also be further increased by subjecting the workpiece in which the fuel flow channel for circulating or storing fuel under high pressure is defined in the process. autofrettage.
    Below, the reasons for the limitation of each chemical component and the production conditions of this disclosure are described in detail.
    C: 0.08 to 0.16% C is an element necessary to ensure the resistance, and the carbides of Mo and V are precipitated by the hardening treatment by aging to increase the resistance of the steel. For the action of C, a C content of 0.08% or more is required, and if the C content is less than 0.08%, the required hardness and strength cannot be guaranteed. On the other hand, if the C content exceeds 0.16%, the amount of cementite increases and the toughness deteriorates, so that an upper limit of the C content is set at 0.16%.
    Si: 0.10 to 0.30% [0029] Si is added as a deoxidizer during the melting of the steel and to improve its resistance. For the action of Si, it is necessary to include Si up to 0.10% or more. On the other hand, since an excessive Si content greater than 0.30% results in a reduction in the resistance to fatigue, an upper limit of the Si content is set at 0.30%.
    Mn: 1.00 to 2.00% It is necessary to include Mn up to 1.00% or more to guarantee the hardenability (guarantee a bainitic structure), improve the resistance and improve the '' machinability (crystallization of MnS). However, since an excessive Mn content greater than 2.00% results in the formation of martensite, an upper limit of the Mn content is set at 2.00%.
    S: 0.005 to 0.030% [0033] S must be contained up to 0.005% or more in order to guarantee machinability. However, since an excessive S content greater than 0.030% leads to a deterioration in productivity, an upper limit of the S content is set at 0.030%.
    Cu: 0.01 to 0.30% Cu is included to ensure the hardenability (to guarantee the structure of the bainite) and improve the resistance. For the action of Cu, it is necessary to include Cu up to 0.01% or more. However, since an excessive Cu content greater than 0.30% leads to an increase in costs and a deterioration in productivity, an upper limit of the Cu content is set at 0.30%.
    Ni: 0.40 to 1.50% Ni is an essential component in the present disclosure to guarantee the toughness (fracture toughness), and Ni is included up to 0.40% or more for the action of Ni. However, since an excessive Ni content greater than 1.50% leads to an increase in costs, an upper limit of the Ni content is set at 1.50%.
    Cr: 0.50 to 1.50% [0039] Cr is included to guarantee the hardenability (to guarantee the bainitic structure) and improve the resistance. For the Cr function, it is necessary to include Cr up to 0.50% or more. However, since an excessive Cr content greater than 1.50% leads to an increase in costs, an upper limit for the Cr content is set at 1.50%.
    Mo: 0.30 to 0.70% [0041] Mo is contained because the carbide of Mo is precipitated by an aging hardening treatment to obtain a high resistance. Mo is included at 0.30% or more for the Mo function. However, since an excessive Mo content greater than 0.70% leads to an increase in costs, an upper limit of the Mo content is set 0.70%.
    V: 0.10 to 0.40% As with Mo, V causes precipitation of V carbide by an aging hardening treatment to increase the strength of the steel. It is necessary to include V up to 0.10% or more due to the action of V. However, since an excessive V content, higher than 0.40% leads to an increase in costs, an upper limit the V content is fixed at 0.40%.
    S-Al: 0.001 to 0.100% [0045] S-Al is used for deoxidation during dissolution and is included at least 0.001% or more. In addition, the effect of grain refining by precipitation of AIN leads to an improvement in toughness. However, since the excessive precipitation of AIN causes deterioration of the machinability, an upper limit of the s-Al content is set at 0.100%.
    S-Al represents an acid-soluble aluminum and is quantified by a method disclosed in Annex 15 to standard JIS G 1257 (1994). The content of JIS G 1257 (1994) is incorporated here by reference.
    Forging heating temperature: 950 to 1350 ° C. In order to obtain a bainitic single-phase structure, it is necessary to heat the part to 950 ° C. or more during hot forging. Indeed, when the forging heating temperature is below 950 ° C, ferrite is easily generated in the structure after forging. However, taking into account that excessive heating causes damage to a heat treatment furnace and an increase in the energy cost, the forging heating temperature is set at 1350 ° C or lower.
    Average cooling rate of 800 ° C to 500 ° C: 0.1 l ° C / s or more To avoid the appearance of any ferrite-perlite transformation during cooling after hot forging, the average cooling rate of 800 ° C to 500 ° C should be set at 0.1 ° C / s or more. More preferably, the average cooling rate is set at 0.2 ° C / s or more.
    On the other hand, an upper limit of the average cooling rate is not particularly limited, but taking into account the capacity of the installation and the continuity with subsequent cooling to 500 ° C. or less, it is best to cool to 10 ° C / s or less.
    Average cooling rate of 500 ° C to 300 ° C: 0.02 to 10 ° / s [0053] If the average cooling rate of 500 ° C to 300 ° C is excessively slow, coarse cementite precipitates in the bainitic structure and the toughness decreases. For this reason, the average cooling rate of 500 ° C to 300 ° C is set to 0.02 ° C / s or more. On the other hand, when the average cooling rate of 500 ° C to 300 ° C is excessively high, a martensitic transformation occurs and the hardness to be forged becomes too high, so it is necessary to adjust the speed of average cooling to 10 ° C / s or less. A more preferable range of the average cooling rate is defined between 0.4 and 5 ° C / s [0054] Area ratio of the bainitic structure: 85% or more [0055] When 15% or more of a structure other than bainite is mixed in the bainitic structure, not only the aging hardening characteristics are deteriorated, but also the bearing capacity ratio and the durability ratio are deteriorated, which can lead to the deterioration of fatigue resistance. For this reason, the surface ratio of the bainitic structure is fixed at 85% or more. More preferably, the area ratio is 90% or more.
    Ti: <0.100% [0057] Nb: <0.100% [0058] Ti precipitates the carbide of Ti by the hardening treatment by aging and contributes to further increase the resistance. In addition, since the miniaturization of MnS by precipitation of TiN contributes to an improvement in processability, Ti can be included if necessary. However, since an excessive Ti content greater than 0.100% decreases the toughness, the upper limit of the Ti content is fixed at 0.100%. When Ti is included, the Ti content is preferably 0.005% or more.
    The Nb precipitates the carbide of Nb by hardening treatment by aging and contributes to further increase the resistance. However, since an excessive Nb content greater than 0.100% decreases the toughness, the upper limit of the Nb content is fixed at 0.100%. When Nb is included, the Nb content is preferably 0.005% or more.
    Only one of Ti and Nb can be included, but both of Ti and Nb can be included.
    Maximum diameter of non-metallic inclusions: not more than 300 μm [0062] Non-metallic inclusions present in the steels are effective in inhibiting the growth of austenite grains during hot forging, but too large inclusions become a starting point of fatigue failure and reduce the fatigue strength, so that an upper limit of the maximum diameter ^ area m . 1x non-metallic inclusions are set at 300 µm. The maximum diameter ^ arca, n ., X can be obtained on the basis of a statistical method of extreme values described in the Non-Patent Document 1 below.
    [Non-Patent Document 1] Keiji Murakami: Effects of Metal Fatigue Defects and Intermediaries (1993), [YOKENDO] [0064] Aging treatment temperature: 550 ° C to 700 ° C [0065] In the present disclosure, fine carbides can be precipitated from the steel by performing an aging treatment after hot forging, and the strength can be increased. However, when the aging treatment temperature is excessively low, the amount of precipitated carbide is small and a sufficient effect cannot be obtained, so that the aging treatment temperature is preferably set at 550 ° C or more.
    On the other hand, when the aging treatment temperature is higher, the precipitated carbide becomes coarser. In addition, since the bainite is inversely transformed into austenite at the time of the aging hardening treatment, and that part of the austenite is martensitized during the subsequent cooling, a martensite phase is generated around an austenite. residual in the form of an island to significantly reduce the toughness, it is preferable that the aging treatment temperature is set at 700 ° C. or less.
    BRIEF DESCRIPTION OF THE DRAWINGS Other characteristics, details and advantages of the invention will appear on reading the detailed description below, and on analysis of the appended drawings, in which: FIG. IA [fig.lA] is a vertical sectional view showing a common ramp to which a manufacturing process of the present embodiment is applied,
    Fig. IB [fig.lB] is a horizontal sectional view showing the common rail;
    Fig. 2 [fig.2] is an illustrative view showing the hot forging of the manufacturing process according to the present embodiment.
    Description of the embodiments Hereinafter, a manufacturing method according to an embodiment of the present disclosure will be described. [Fig.lA] and [Fig. IB] showing a common rail 10 as a fuel injection component. The common rail 10 is a component intended to accumulate high pressure fuel to be supplied to an injector for injecting fuel into a cylinder of an internal combustion engine such as a diesel engine. As illustrated in [Fig. IA] and in [Fig. IB], the common rail 10 has a body part 12 extending linearly in one direction and multiple parts of connection cylinders 14 provided so as to protrude from a lateral surface of the body part 12. A main hole 16 used as a fuel pressure accumulation chamber is defined inside the body part 12 in a longitudinal direction of the body part 12. On the other hand, a small hole 20 is defined at the interior of each of the connection cylinder portions 14 so that one end of the connection cylinder portion 14 communicates with the main hole 16. The main hole 16 and the small holes 20 define a fuel flow channel for making circulate or store fuel under high pressure.
    Two internal threaded portions 17 are formed at both ends of the body portion 12, and male threaded portions 22 are formed on external peripheral surfaces of ends of the portions of the respective connection cylinders 14, and the female threaded portions 17 and the external threaded portions 22 can be attached and fixed to the respective coupling element.
    The common rail 10 described above can be manufactured by performing steps of a process of hot forging, machining, aging and autofrettage in the order indicated, for example, with the use of a part having a predetermined chemical composition. The part to be used for hot forging can be a billet obtained by rolling ingot blocks, a billet obtained by rolling a mass of a continuous casting material, a steel bar obtained by hot rolling or by hot forging of these billets, or the like.
    During hot forging, as shown in [fig.2], the workpiece is first heated to a predetermined forging heating temperature (950 to 1350 ° C). Then, hot forging is carried out on the part heated to a part temperature of 950 to 1250 ° C. using a mold so as to obtain an external shape such as the common rail 10.
    Once the hot forging is complete, the part is cooled to approximately room temperature. In this example, the part is cooled in a temperature range of 800 ° C to 500 ° C at an average cooling rate of 0.1 ° C / s or more, and in a subsequent temperature range of 500 ° C to 300 ° C to 0.02 ° C / s or more and 10 ° C / s or less, and the steel structure after hot forging is placed in a bainitic single-phase structure. In this example, the average cooling rate is an average cooling rate on a part surface.
    Cooling is carried out by cooling in the atmosphere or by cooling to the incident air by means of a fan. The cooling conditions for meeting the above-mentioned specification of the average cooling rate vary depending on the ambient temperature, the shape and size of the workpiece, and the like, and therefore it is desirable to determine experimentally the cooling conditions in advance.
    The part, which has been formed to achieve the substantially external shape of the common rail by hot forging, is then machined, for example by cutting, to form the internal fuel flow channels 16 and 20, as well as the female threaded parts 17, the male threaded parts 22 and the like. In order to perform the machining satisfactorily, it is desirable to set the hardness of the workpiece after hot forging at 33 HRC or less.
    Then, the aging treatment is carried out at a central room temperature of 550 ° C to 680 ° C for 0.5 to 10 hours to obtain the desired hardness.
    Next, an autofrettage process is performed on the part in which the fuel flow channels 16 and 20 for circulating or storing the fuel under high pressure are provided. More specifically, in order to seal the fuel flow channels 16 and 20, an end portion of each of the connection cylinder portion 14 and the body portion 12 is sealed, a pressure application material ( hydraulic oil) is introduced into the main hole 16 from the other end side of the body portion 12, and the introduced pressure application material is pressurized. At this time, a pressure of the pressure application material is set to a pressure (e.g., from about 500 MPa to 1000 MPa) to plastically deform the interior of the body portion 12 and elastically deform the exterior of the body part 12. Consequently, a residual compressive stress can be applied inside the body part 12 and a fatigue strength of the pressure resistance of the body part 12 can be improved.
    The common rail 10 can be manufactured by the above methods. In some cases, the aging process and the autofrettage process can be omitted as required, for example, the aging treatment is omitted by increasing the hardness of the hot work as it is. The machining process can be carried out separately before and after the autofrettage process, or an external treatment such as applying a coating can be added.
    150 kg of types A to M steel (13 types) having the chemical compositions indicated in Table 1 below are melted in a vacuum induction melting furnace and forged into a round bar having a diameter d '' about 60 mm at 1250 ° C. Then, the 60 mm round bar is heated to 950 ° C or more and to 1350 ° C or less in accordance with the manufacturing conditions shown in Table 2, subjected to a hot forging process in which the round bar is forged at hot in a shape corresponding to the common rail, then cooled from a temperature at the end of forging to about room temperature to obtain a hot forged material. Then, the evaluation of the inclusion, the observation of the microstructure and the hardness test are carried out using the hot forged material. Additional machining is performed to produce a common rail, and the fatigue strength under internal pressure and the burst strength are assessed.
    Chemical composition (% by mass, Fe residue) [Tables 1]
    typed 'Steel VS Yes mn S Cu Or Cr MB V s-Al Other AT 0.13 0.21 1.40 0,022 0.10 0.61 1.00 0.60 0.33 0,021B 0.09 0.20 1.30 0,029 0.09 0.60 1.01 0.70 0.21 0,023 0.010 Ti;0.01 Nb VS 0.11 0.11 1.78 0,030 0.09 0.41 1.01 0.31 0.39 0,018 0.096 Ti D 0.15 0.21 1.40 0.012 0.10 0.61 1.00 0.70 0.11 0,025 0.090 Ti E 0.13 0.30 1.43 0.005 0.09 0.60 1.26 0.31 0.33 0,025F 0.15 0.20 1.00 0,022 0.09 0.41 1.48 0.60 0.21 0,021 0.01 Nb G 0.13 0.30 2.00 0.005 0.09 0.98 0.75 0.31 0.21 0,020H 0.15 0.24 1.00 0.005 0.09 0.98 1.10 0.60 0.33 0,025I 0.12 0.30 1.90 0,022 0.09 0.60 0.50 0.60 0.30 0,038J 0.15 0.24 1.90 0.012 0.28 0.87 1.00 0.60 0.20 0,021K 0.12 0.21 1.40 0.012 0.10 0.55 1.00 0.60 0.33 0.033The 0.10 0.20 1.50 0.012 0.10 0.61 1.20 0.60 0.21 0,036M 0.10 0.21 1.20 0.012 0.10 0.51 0.52 0.44 0.30 0.031
    [Paintings!]
    T Manufacturing conditions Evaluationyp You bind Second tail You Tr LPs Duret Duret Vale resis Rese MPE quickly s s th the MPE has o-str é pre- ed ur tance istaof ratu e of speed of the ratu e uctur aged after of to the nceac re refroi to re- incl re m e sows aged tough fatig to theier of disse froidis Usio of in (ratio nt (H sseme ty (H eu rupt cha is lying semen ns (/ i Viei t baini RC) nt (H RC) under ure uffa moye t m) lliss AT tickRC)press through ge detached moyeth F ) ion lighti (° C) (° C / s) detachedntinter tem (° C / s)(° C)born ent
    Ex em pie 1 AT 1200 1.8 0.6 28 625 - 0(100%) 30.9 36.1 5.2 0 0 2 AT 1300 2.0 0.9 28 625 - 0(100%) 31.4 35.8 4.4 0 0 3 AT 960 1.9 0.9 28 625 - 0(100%) 30.1 34.7 4.6 0 0 4 AT 1200 0.6 0.4 28 625 - 0(100%) 29.9 35.0 5.1 0 0 5 AT 1200 1.8 0.02 28 625 - 0(100%) 30.3 36.0 5.7 0 0 6 B 1200 2.1 1.0 32 625 - 0(100%) 28.5 33.5 5.0 0 0 7 VS 1200 1.8 0.9 34 625 - 0(100%) 29.7 35.0 5.3 0 0 8 D 1200 2.0 0.6 30 625 - 0(100%) 30.0 33.9 3.9 0 0 9 E 1200 2.0 0.9 24 625 - 0(100%) 31.0 34.8 3.8 0 0 10 F 1200 1.9 0.7 21 625 - 0(100%) 31.5 34.4 2.9 0 0 11 G 1200 1.9 0.6 22 625 - 0(100%) 30.9 35.0 4.1 0 0 12 H 1200 2.2 1.0 21 625 - 0(100 30.9 37.0 6.1 0 0
    %)13 I 1200 2.0 0.8 33 625 - 0(100%) 30.4 35.6 5.2 0 0 14 K 1200 3.1 1.4 101 625 - 0(100%) 30.8 36.0 5.2 0 0 15 The 1200 1.9 1.0 331 625 - 0(100%) 31.1 34.0 2.9 0 0 16 AT 1200 4.1 2.5 28 530 - 0(100%) 31.2 33.5 2.3 0 0 17 AT 1200 4.0 2.4 28 550 - 0(100%) 30.4 34.5 4.1 0 0 18 AT 1200 4.2 2.9 28 680 - 0(100%) 30.3 34.6 4.3 0 0 19 AT 1200 4.0 2.5 28 700 - 0(100%) 31.3 33.0 1.7 0 0 20 J 1200 4.2 2.3 33 - - 0(100%) 35.5 - - 0 0 211200 2.0 0.8 28 625 0 0(100%) 31.2 36.0 4.9 0 0
    Ex em pieCo mp arat if 1 AT 930 0.4 0.4 28 625 - XL(80%) 27.1 32.4 5.3 X X 2 M 1200 0.08 0.4 28 625 - XL(75%) 22.5 26.0 3.5 X X 3 AT 1200 2.0 0,015 28 625 - O(100%) 29.5 34.5 5.0 X X
    In the cooling treatment, the surface temperature of the part is measured by a radiation thermometer, and the average cooling rate from 800 ° C to 500 ° C is determined as the first average cooling rate, and the average cooling rate from 500 ° C to 300 ° C is determined as the second average cooling rate, and the results are shown in Table 2.
    <Evaluation of inclusions>
    The maximum diameter ^ arca, n ., X of non-metallic inclusions in the 3000 mm2 estimated by the statistical method of extreme values is obtained by observing a cross section of the hot forged material parallel to a longitudinal direction using of an optical microscope.
    The maximum diameter 'Varea max of non-metallic inclusions can be obtained as follows on the basis of the measurement method described in Document Non Patent 1 described above.
    [1] After polishing a cross section of the hot forged material parallel to the longitudinal direction, a test reference area S0 (mm2) is determined with the polished surface as the test area.
    [2] A non-metallic inclusion occupying a maximum surface in S0 is selected and a square root ^ arca, n ., X (pm) of the surface of the non-metallic inclusion is measured.
    [3] The measurement is repeated n times to avoid duplication of the inspection part.
    [4] The measured values ^ arca, n ., X are reorganized in ascending order, and each is fixed at 'Varea maXjj (j = 1 to n).
    [5] For each j, the following normalized variable yj is calculated.
    Yj = -ln [-ln {j / (n + l)}] [6] In the coordinates of a statistical document of extreme values, ^ area m . lx is chosen on the abscissa, and the normalized variables are chosen on the ordinate and j = 1 to n are plotted, and an approximate straight line is obtained by the method of least squares.
    [7] If the area to be evaluated is S (mm2) and a recursive period is T = (S + S o ) / S o , the value of y is obtained from Γ Expression (1) below , and the ^ area m . lx for the value of y is calculated using the approximate curve described above, the maximum diameter of the non-metallic inclusion in the area S to be evaluated is' Varea max .
    Y = -ln [-ln {(Tl) / T}] [Expression (1) [0096] In this example, the tests with the test reference area S0 = 100 mm2 and the number of tests n = 30 times are carried out to determine the maximum diameter Varea max of non-metallic inclusions in the 3000 mm2, and the results are presented in Table 2.
    <Hardness Test>
    The hardness test is carried out on a load of a 150 kgf conical diamond penetrator with a Rockwell hardness tester according to JIS Z 2245. The measurement is carried out at a position having a radius of 1/2 of the forged material hot.
    CObservation of the Microstructure>
    For the observation of the microstructure, a longitudinal cross section of the hot forged material is observed under an optical microscope (magnification: 400X) after corrosion with Nital and the bainitic ratio is measured. Concerning the bainitic ratio, the evaluation of O is made when the surface ratio of the bainitic structure is equal to or greater than 85%, the evaluation of XF is made in the case of the mixture of the bainitic structure and the ferritic structure ( the surface ratio of the ferritic structure is 15% or more) and the results are presented in Table 2.
    In the table, the area ratio of the bainite actually measured is also indicated in brackets, in addition to the evaluation of O and X.
    [Fatigue resistance under internal pressure>
    Then, the hot forged material is provided with the main hole 12 and small holes 20a to 20th by cutting (see FIG. IA and IB), and a test piece for the fatigue test under internal pressure is produced, and after that the hot forged material has been heated to the temperatures indicated in Table 2 for 1 hour and subjected to the aging treatment, the fatigue test under internal pressure is carried out. A pressure generation source is connected to the small holes 20a of the test piece and a pressure sensor is provided in the middle of the connection. Once the end parts of the other small holes 20b to 20e and the two ends of the main hole 12 have been closed, oil is allowed to flow from the small hole 20a connected to the pressure generation source of so as to periodically modify a stress, and the resistance to fatigue by the rate of repetition of the internal pressure is the subject of a comparison and an evaluation, and the results are presented in Table 2. In Table 2, a case in which the fatigue strength is greater than that of a test piece of non-heat treated steel of the ferrite-perlite type which has been subjected to the similar test is designated by O and a case where the resistance the fatigue is lower than that of the non-heat treated ferriteperlite type steel test piece is designated by X.
    <Resistance to rupture by bursting>
    The hot forged material is provided with the main hole 12 and small holes 20a to 20e by cutting (see [fig.lA] and [Fig. IB]), test pieces for the burst rupture strength test. are produced, and the test pieces are subjected to the aging treatment by heating at the temperatures indicated in Table 2 for 1 hour, then subjected to the burst rupture strength test. A pressure generation source is connected to the small holes 20a of the test piece and a pressure sensor is provided in the middle of the connection. Once the end parts of the other small holes 20b to 20e and the two ends of the main hole 12 have been closed, oil is allowed to flow from the small hole 20a connected to the pressure generation source of In order to temporarily modify the stress incrementally, and the burst strength due to static internal pressure is compared and evaluated, and the results are presented in Table 2.
    The test pressure is fixed at 300 MPa or more, and in Table 2, a case in which the burst strength is greater than that of the test piece of non-heat treated steel of the ferrite-perlite type. which has been subjected to the similar test is designated by O and a case where the bursting strength is lower than that of the test piece of non-heat treated steel of ferriteperlite type is designated by X.
    In the results of Table 2, in Comparative Example 1, the forging heating temperature is less than 950 ° C, which is a lower limit value of the present disclosure, and the steel structure is a structure mixed with ferrite. Consequently, the hardness after the aging treatment is lower than that of the examples, and the results of the fatigue strength under internal pressure and the burst strength are both X.
    In Comparative Example 2, the average cooling rate (first average cooling rate) from 800 ° C to 500 ° C is less than 0.1 ° C / s, which is a lower limit value of the present disclosure, and the steel structure is a structure mixed with ferrite. Still in Comparative Example 2, the hardness after the aging treatment is lower than that of the examples, and the results of the resistance to fatigue under internal pressure and the resistance to rupture by bursting are both X.
    Comparative Example 3 is an example in which the average cooling rate of 500 ° C to 300 ° C (second average cooling rate) is less than the lower limit value of 0.02 ° C / s of the this disclosure. In Comparative Example 3, the steel structure is a bainitic single-phase structure and the hardness after aging treatment is obtained in the same proportions as in the examples, but the results of the resistance to fatigue by internal pressure and of the resistance at bursting are both X. It is assumed that this is due to the fact that the cementite precipitated in the bainitic structure becomes coarse due to the weakness of the second average cooling rate.
    On the other hand, in Examples 1 to 21 satisfying the conditions of the present disclosure, the evaluation of both the resistance to fatigue under internal pressure and the resistance to rupture by bursting is 0, and excellent results are obtained. In other words, the fuel injection component to which a high internal pressure is repeatedly applied is manufactured with the use of the steel material having the composition of the present disclosure under the manufacturing conditions described above, the resistance higher than the holding pressure can be ensured, and the fragile rupture, which is an instantaneous rupture when a maximum operating pressure or an abnormally high pressure is applied, can be avoided. In particular, the toughness at low temperatures can be improved.
    In Example 20, the hardness of hot forging is increased and the aging treatment is omitted. Example 21 is an example in which the autofrettage process (AF processing) is performed after machining. Excellent results are obtained for Examples 20 and 21 in the same manner as in the other examples.
    The above detailed description of the embodiments and examples of the present disclosure has been presented by way of example only. Although the common rail is illustrated in the embodiments and examples above, the present disclosure can be implemented according to various variants without departing from its spirit, by applying it for example to other injection components of fuel.
    For any useful purpose, the following non-patent document is cited:
    - [Non-Patent Document 1] Keiji Murakami: Effects of Metal Fatigue Micro-Defects and Intermediaries (1993), [YOKENDO];
    - [Non-Patent Document 2] Annex 15 to the JIS G 1257 standard (1994).
    For any useful purpose, the following patent documents are cited:
    - [Patent Document 1] JP 5778055 B;
    - [Patent Document 2] JP 2012-246527 A.
    权利要求:
    Claims (1)
    [1" id="c-fr-0001]
    claims [Claim 1] A method of manufacturing a fuel injection component by working on a workpiece to a predetermined shape, wherein the workpiece is made of steel having compositions, in% by mass, ofC: 0.08 to 0.16%,If: 0.10 to 0.30%,Mn: 1.00 to 2.00%,S: 0.005 to 0.030%,Cu: 0.01 to 0.30%,Ni: 0.40 to 1.50%,Cr: 0.50 to 1.50%,Mo: 0.30 to 0.70%,V: 0.10 to 0.40%,s-Al: 0.001 to 0.100% andFe and unavoidable impurities as residual components,the process comprising:subjecting the workpiece to hot forging after heating the workpiece to a temperature of 950 ° C or more and 1350 ° C or less;a first cooling of the part, after hot forging, at an average cooling rate of 0.1 ° C / s or more in a temperature range from 800 ° C to 500 ° C; anda second cooling of the part, after the first cooling, at an average cooling rate of 0.02 ° C / s or more and 10 ° C / s or less in a subsequent temperature range from 500 ° C to 300 ° C to establish an area ratio of a bainitic structure after hot forging of 85% or more. [Claim 2] The method according to claim 1, in which the steel additionally contains one or two of Ti: <0.100% and Nb: <0.100% by mass%. [Claim 3] The method of claim 1 or 2, wherein a maximum diameter 'Varea max of non-metallic inclusions, estimated by a statistical method of the extreme values in the workpiece after hot forging, is 300 µm or less. [Claim 4] The method according to any of claims 1 to 3, further comprising performing, after hot forging, an aging treatment in a temperature range of 550 ° C to 700 ° C.
    [Claim 5] The method of any of claims 1 to 4, further comprising performing an autofrettage process on the workpiece in which a fuel flow channel is formed. [Claim 6] The method according to any of claims 1 to 5, further comprising performing machining on the workpiece. [Claim 7] The method according to any of claims 1 to 5, further comprising:- the execution of a machining on the part from a fuel flow channel in the part; and-the execution of an autofrettage process on the fuel flow channel of the part.
    1/2
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    同族专利:
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    JP2019210530A|2019-12-12|
    US10947943B2|2021-03-16|
    DE102019114268A1|2019-12-12|
    US20190376479A1|2019-12-12|
    CN110578086A|2019-12-17|
    引用文献:
    公开号 | 申请日 | 公开日 | 申请人 | 专利标题
    FR2780418B1|1998-06-29|2000-09-08|Aubert & Duval Sa|CEMENTATION STEEL WITH HIGH INCOME TEMPERATURE, PROCESS FOR OBTAINING SAME AND PARTS FORMED THEREFROM|
    ES2677594T3|2007-11-12|2018-08-03|Nippon Steel & Sumitomo Metal Corporation|Method for producing common ducts and partially reinforced common ducts|
    JP5620336B2|2011-05-26|2014-11-05|新日鐵住金株式会社|Steel parts for high fatigue strength and high toughness machine structure and manufacturing method thereof|
    JP5778055B2|2012-02-15|2015-09-16|新日鐵住金株式会社|ROLLED STEEL FOR HOT FORGING, HOT FORGING SEMICONDUCTOR, COMMON RAIL AND PROCESS FOR PRODUCING THE SAME|
    WO2015133470A1|2014-03-05|2015-09-11|大同特殊鋼株式会社|Age hardening non-heat treated bainitic steel|
    JP6070617B2|2014-04-03|2017-02-01|Ｊｆｅスチール株式会社|Seamless steel pipe for fuel injection pipes with excellent internal pressure fatigue resistance|US10392537B2|2016-07-01|2019-08-27|H.B. Fuller Company|Propylene polymer-based hot melt adhesive composition exhibiting fast set time and articles including the same|
    WO2021117243A1|2019-12-13|2021-06-17|日本製鉄株式会社|Age hardening steel, steel and mechanical component|
    法律状态:
    2020-06-19| PLFP| Fee payment|Year of fee payment: 2 |
    优先权:
    申请号 | 申请日 | 专利标题
    JP2018109766A|JP2019210530A|2018-06-07|2018-06-07|Manufacturing method of fuel injection component|
    JP2018-109766|2018-06-07|
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