EP1550736A1 - Carburized and quenched member and method for production thereof - Google Patents
Carburized and quenched member and method for production thereof Download PDFInfo
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- EP1550736A1 EP1550736A1 EP02790874A EP02790874A EP1550736A1 EP 1550736 A1 EP1550736 A1 EP 1550736A1 EP 02790874 A EP02790874 A EP 02790874A EP 02790874 A EP02790874 A EP 02790874A EP 1550736 A1 EP1550736 A1 EP 1550736A1
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- carburized
- quenching
- hardened member
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/20—Carburising
- C23C8/22—Carburising of ferrous surfaces
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/80—After-treatment
Definitions
- the present invention relates to a carburized and hardened member that is excellent in fatigue strength and dimensional accuracy, and a production method for the member.
- carburized and hardened members subjected to a carburizing and quenching process are often used in order to increase the surface hardness and the toughness.
- Conventional carburized and hardened members are normally produced by forming a case hardening steel (JIS: SCM420H, SCR420H, SNCM220) or the like into a desired shape, and then gas-carburizing the steel in a carburizing atmosphere, and then quenching it in an oil or the like.
- JIS Japanese Industrial Standard SCM420H, SCR420H, SNCM220
- One of goals regarding the carburized and hardened members is to further improve the post-carburizing and quenching process strength and, at the same time, improve the dimensional accuracy by reducing or suppressing the hardening strain.
- the present invention has been accomplished in view of the aforementioned problems of the conventional art. It is an object of the present invention to provide a carburized and hardened member that allows strength enhancement while sufficiently reducing the hardening strain, and a production method for the carburized and hardened member.
- a first aspect of the present invention is a carburized and hardened member production method characterized in: that an alloy steel which contains Fe as a main component and contains 0.10 to 0.50 wt.% of C and 0.50 to 1.50 wt.% of Si and whose hardenability J based on an end quenching test is in a range of 35 to 50 (at 12.5 mm) is used as a raw material; and that after the material is formed into a member of a desired shape, a carburized layer is formed by performing a carburizing process in an oxidation inhibitive atmosphere; and that after the carburizing process, a quenching process is performed in such a condition that cooling is monotonously performed from a pearlite transformation point (A1 point) to a martensite transformation start point (Ms point), and such a condition that a severity of quenching H is in a range of 0.01 to 0.08 (cm -1 ).
- the aforementioned hardenability J based on an end quenching test is a value acquired by an end quenching test method prescribed in JIS: G0561 (generally termed "Jominy end quench test method"). Furthermore, the indication of (at 12.5 mm) means that the value of hardenability J is a value of hardenability J regarding a position of 12.5 mm from the water cool-side end surface of a rod-like test piece in the Jominy end quench test method.
- a specific alloy of which the C content and the Si content and the hardenability J are within the specific ranges is used as a raw material.
- the quenching process is performed so as to fulfill the aforementioned conditions of monotonous cooling and the aforementioned condition of specific severity of quenching H. That is, only after the material characteristics and the production conditions are fulfilled, it becomes possible to provide a carburized and hardened member in which the strength is enhanced while the hardening strain is sufficiently reduced.
- the setting of the C content within the range of 0.1 to 0.50 wt.% makes it possible to secure an appropriate toughness and an appropriate strength of a non-carburized portion (internal portion) after the carburizing and quenching process. If the C content is less than 0.1 wt.%, the aforementioned effect is not sufficient. If the C content exceeds 0.50 wt.%, the pre-quenching hardness becomes excessively high, thus creating a possibility of increased processing cost and reduced toughness. Furthermore, due to increased structural transformation rate of the interior of the non-carburized portion following the carburizing and quenching process, transformation stress increases, and due to great quenching strain, the component part accuracy may degrade.
- the member positively contains Si as a component, and the content thereof is 0.50 to 1.50 wt.%.
- the carburizing process is performed in an oxidation inhibitive atmosphere. Therefore, it becomes possible to achieve improved plane fatigue strength, improved hardenability, improved resistance to temper softening, etc. while reducing the intergranular oxidation, which is likely to occur at the time of the carburizing process.
- the Si content is less than 0.50 wt.%, the aforementioned improvement effect is small; in particular, there is a problem of reduction of intergranular oxidation preventative effect at the time of the carburizing process. Conversely, if the Si content is greater than 1.50 wt.%, the improvement effect becomes saturated, and uniform austenitization prior to quenching is difficult. In order to prevent or curb degradations in the plastic processability, the cutting processability and the formability of the material, it is preferable that the Si content be less than or equal to 0.70 wt.%. Therefore, a preferable range of the Si content is a range greater than 0.50 wt.% and less than or equal to 0.70 wt.%.
- the hardenability J of the material is limited within the range of 35 to 50 (at 12.5 mm). Therefore, excellent hardening effect can be achieved even if the range of the severity of quenching H is limited to the aforementioned range. If the hardenability J is less than 35, it becomes impossible to achieve sufficient hardening effect on the carburized layer and the non-carburized portion (internal portion) in the quenching process following the carburizing process, and it is therefore impossible to achieve a desired strength enhancement. Therefore, it is preferable that the hardenability J be greater than or equal to 38. If the hardenability J exceeds 50, the structural transformation rate of the internal portion, that is, the non-carburized portion, rises, so that the transformation stress increases and the hardening strain becomes more likely.
- hardenability J If the hardenability J is higher, the hardness prior to the carburizing and quenching process is correspondingly higher, so that processability, such as the plastic processability prior to the carburizing process, the cutting processability, etc., degrades. Therefore, in order to prevent such degradation of workability, it is preferable that hardenability J be less than or equal to 45.
- the severity of quenching H is limited within the range of 0.01 to 0.08 (cm -1 ). If the alloy having the specific amount of carbon and having the hardenability is used, it becomes possible to substantially prevent or reduce the hardenability strain at the time of hardening process and therefore secure excellent dimensional accuracy.
- the severity of quenching H is less than 0.01 (cm -1 ), it is impossible to achieve sufficient hardening effect on the carburized layer and the non-carburized portion (internal portion) in a hardening process following the carburizing process as in the case where the hardenability J is less than 35. Therefore, desired strength enhancement cannot be accomplished. If the severity of quenching H is greater than 0.08 (cm -1 ), the transformation stress increases due to, particularly, increased structural transformation rate of the internal portion, that is, the non-carburized portion, and therefore the hardening strain is likely to occur, as in the case where the hardenability J is greater than 50.
- the quenching process is performed under the condition that the cooling monotonously occurs from the A1 point to the Ms point, in addition to the condition of the range of severity of quenching H.
- the term "monotonously" herein means that re-heating is not performed during the cooling process, that is, there is no rise of the material temperature during the cooling. Therefore, examples of the case where the condition of monotonous cooling is fulfilled include a case where the material temperature continues to fall, and a case where if the temperature stops falling during the process, the temperature remains constant and never rises, and then starts falling again. Furthermore, changes in the cooling rate are allowable.
- the monotonous cooling condition it is possible to select a cooling condition such that the cooling does not enter a region of a nose of an S curve indicated in an isothermal transformation diagram within the carburized portion. This selection secures sufficient martensite transformation.
- the present invention provides a carburized and hardened member in which the strength is enhanced while the hardening strain is sufficiently reduced, as the invention comprises the aforementioned C content, the Si content, the hardenability J, the carburizing process in an oxidation inhibitive atmosphere, and the quenching process that fulfills the condition of the monotonous cooling and the condition of the specific severity of quenching H. If any one of these elements is absent, the intended object cannot be achieved.
- the present inventors have discovered this through many experiments.
- a second aspect of the present invention is a carburized and hardened member produced by the above-described production method, characterized in that a surface hardness of the carburized layer is in a range of 700 to 900 Hv, and an internal hardness of a non-carburized portion located inward of the carburized layer is in a range of 250 to 450 Hv.
- This carburized and hardened member is produced by adopting the above-described production method and by adjusting the component range processing condition so as to restrict the surface hardness of the carburized layer and the internal hardness of the non-carburized portion within the aforementioned ranges. Therefore, it becomes possible to secure a static strength (tensile strength, flexural strength, torsional strength, etc.) and a dynamic strength (plane fatigue strength, bending fatigue strength, torsion fatigue strength, etc.) in a region from the surface to the internal portion (core portion), with respect to the distribution of stress applied to the member which results from the operating stress caused on the member by load applied to the member and the stress concentrated adjacent to the surface of the member due to bumps and dips, holes, etc. of the member.
- a static strength tensile strength, flexural strength, torsional strength, etc.
- a dynamic strength plane fatigue strength, bending fatigue strength, torsion fatigue strength, etc.
- the surface hardness of the carburized layer is less than 700 Hv, a conceivable problem is that strength cannot be secure corresponding to the stress concentration adjacent to the surfaces of the member. Another conceivable problem is insufficient abrasion resistance in outermost surface. If the surface hardness is greater than 900 Hv, production of carbide, such as cementite and the like, in the surface layer is conceivable. Therefore, a conceivable problem is insufficient strength and, more particularly, reduced toughness.
- the internal hardness of the non-carburized portion is less than 250 Hv, the problem of insufficient strength and, more particularly, insufficient static strength, can be considered. If the internal hardness is greater than 450 Hv, the following problem is possible, taking the rate of transformation of structure into consideration. That is, when a hardening process is performed so as to secure 450 Hv, a great transformation stress occurs, which causes a great hardening strain and therefore makes a factor of degradation in component parts accuracy.
- the carburizing process be performed in a reduced-pressure atmosphere having a reduced pressure of 1 to 30 hPa. Therefore, it becomes possible to easily provide the oxidation inhibitive atmosphere through pressure reduction, and therefore sufficiently prevent intergranular oxidation at the time of carburization.
- the value of the reduced pressure of the reduced-pressure atmosphere being less than 1 hPa is excessive for substantial prevention of oxidation. If such value of the reduced pressure is required, the device for the pressure reduction needs to have high capability for pressure reduction, and creates a problem of cost increase. If the value of the reduced pressure is higher than 30 hPa, the oxidation preventing effect degrades, and furthermore, other problems, such as production of soot in the carburizing furnace, and the like, occur.
- the carburizing process be performed in an atmosphere containing an inert gas as a main component.
- an inert gas examples include nitrogen gas, argon gas, etc.
- the carburizing process be performed so that a surface carbon amount in the carburized layer becomes 0.6 to 1.5 wt.% (claim 4).
- the surface carbon concentration in the carburized layer affects the surface hardness of the carburized and hardened member. If the surface carbon amount in the carburized layer is less than 0.6 wt.%, there occurs a problem of insufficient surface hardness. If the surface carbon amount is greater than 1.5 wt.%, the precipitation of carbide becomes great so that the hardenability of the base remarkably degrades and the surface hardness becomes insufficient.
- intergranular oxidation progressing from a surface of the raw material be at most 3 ⁇ m. That is, it is preferable to restrict the intergranular oxidation to 3 ⁇ m or less from the surface by adjusting the oxidation inhibitive atmosphere, the heating temperature, the heating time, etc., at the time of carburization.
- the intergranular strength decreases if an intergranular oxide (portion) is produced. Therefore, if intergranular oxidation reaches a depth beyond 3 ⁇ m, there is a danger of reduced abrasion resistance due to insufficient strength of the member, reduced hardness, etc. Furthermore, at the time of intergranular oxidation, surrounding alloy elements are also taken up into the intergranular oxide due to chemical reactions. Therefore, the hardenability-improving elements in the carburized and hardened layer around intergranular oxides are taken up and consumed by the intergranular oxides, thereby forming regions where additives are depleted, around the intergranular oxide layer. Therefore, the hardenability of the carburized and hardened layer becomes insufficient. Hence, there is a danger of causing insufficient hardness and insufficient strength.
- the raw material have a surface compression residual stress of 300 to 800 MPa. That is, it is preferable to set the surface compression residual stress to at least 300 MPa by adjusting the composition of the raw material, the oxidation inhibitive atmosphere for the carburization, the heating temperature, the heating time, etc. Therefore, the tensile stress near the surface can be reduced by the compression residual stress near the surface of the member. In particular, the dynamic strength (planer fatigue strength, bending fatigue strength, torsional fatigue strength) can be improved. If the surface compression residual stress is greater than 800 MPa, it is necessary to increase the cooling rate during the quenching process beyond a limit in order to increase the amount of martensite. Therefore, great hardening strain occurs, and therefore a dimensional accuracy of the member cannot be secured.
- the surface compression residual stress can be produced by forming the martensite via the quenching process of the carburized layer, and creating a compression stress field due to volume expansion involved in the transformation.
- the amount of martensite produced is small, that is, if the amount of retained austenite is great, or if the troostite structure is great in amount, it is impossible to form a sufficient compression residual stress field. Therefore, the reduction of the retained austenite (specifically, to 25% or less) and the reduction of the troostite structure (specifically, to 10% or less) are effective in view of enhancement of compression residual stress effect.
- the absorption of volume expansion at the time of martensite transformation does not considerably contribute to enhancement of the surface compression residual stress if the amount of martensite is small.
- the compression residual stress can be increased by performing a surface process, such as shot peening, after the quenching process.
- a surface process such as shot peening
- turning the retained austenite into martensite by the shot peening process is more advantageous in increasing the compression residual stress.
- quenching be performed with the severity of quenching H being in said range during a transition from a temperature in an austenite region to 300°C. Therefore, sufficient quenching effect can be achieved. If the severity of quenching H in a cooling process from the temperature of the austenite region to 300°C is less than 0.01 (cm -1 ), the quenching will be insufficient. Thus, desired hardened structure and characteristic cannot be achieved, and the strength of the member will be insufficient. If the severity of quenching H in a cooling process from the temperature of the austenite region to 300°C is greater than 0.08 (cm -1 ), the quenching will be excessive, so that the structure transformation stress and the thermal stress will increase. Therefore, there is a possibility of increased hardening strain and degraded component part accuracy.
- quenching be accomplished by gas cooling. Therefore, it becomes relatively easy to secure the aforementioned severity of quenching H.
- the quenching by gas cooling use an inert gas. Therefore, a safety can be secured during the quenching.
- the inert gas be a nitrogen gas.
- the adoption of nitrogen gas as the aforementioned inert gas is preferable in view of cost, ease of handling, availability at the time of mass-production operation, etc.
- a retained austenite area rate of the carburized layer preferably is at most 25%. If the retained austenite area rate is greater than 25%, structural transformation from retained austenite into martensite occurs in association with changes in temperature and operating stress during a working process after the carburizing and quenching process, or during the use of the member. Due to the stress of the transformation, strain occurs, and the component parts accuracy will likely degrade. It is more preferable that the retained austenite area rate be 20% or less.
- the retained austenite area rate can be reduced by other manners. For example, the area rate can be reduced by forcibly turning the retained austenite into martensite via shot peening or the like.
- a troostite structure area rate of a surface layer of the carburized layer be at most 10%.
- the troostite is a slack-quenched structure formed in the carburized layer after the carburizing and quenching process, and has a low hardness. Therefore, if the troostite structure area rate is greater than 10%, low-strength troostite will reduce the strength of the component part.
- an internal structure of the carburized and hardened member be bainite. More specifically, it is desirable that the area rate of bainite in a sectional structure be at least 50%. Unlike the case of martensite, transformation of bainite progresses while iron atoms forming a lattice partially diffuse. Therefore, the strain associated with transformation is less in bainite than in martensite. Furthermore, bainite has a greater hardness than pearlite, which is produced if the cooling rate is lower. Thus, bainite appropriately enhances the strength of the internal non-carburized layer.
- the carburized and hardened member be a carburized toothed gear.
- the toothed gears require various strict conditions. The excellent characteristics achieved by the above-described production method are very effective for the toothed gears.
- Step 11 to Steel 14 having chemical compositions shown in Table 1, after being melt-formed in an arc furnace, were hot-rolled into round bars having a diameter of 150 mm and a diameter of 32 mm.
- the round bars were normalized by keeping them at 925°C for an hour and then air-cooling them.
- Steel 11 and Steel 12 are steel grades having new compositions developed in the example.
- Steel 13 and Steel 14 are steel grades corresponding to case hardening steels SCM420 and SNCM 815 according to JIS.
- a hardenability J was determined by conducting a Jominy end quenching method according to JIS: G0561.
- Results are shown in Table 1. This characteristic is a characteristic of a raw material irrelevant to the production method described below.
- Steel grade Component element (wt%) Hardenability J C Si Mn S Ni Cr Mo B Ti Mb A1 N 11 0.16 0.56 0.38 0.012 0.96 1.47 0.01 0.0022 0.044 0.05 0.013 0.006 38 12 0.18 0.75 0.35 0.009 0.71 2.22 0.01 0.0018 0.035 0.03 0.019 0.005 42 13 0.2 0.21 0.78 0.011 0.02 1.01 0.17 - - - 0.027 0.015 25 14 0.15 0.25 0.47 0.009 4.34 0.83 0.27 - - - 0.04 0.018 37
- Steels 11 and 12 are alloy steels that are applicable as a raw material in the present invention in view of material quality and hardenability J.
- the hardenability J and the Si content are outside their respective ranges according to the present invention.
- the Si content is outside the range according the present invention.
- Steels 11 to 14 were formed into round bar test pieces (not shown) of 25 mm in diameter and 50 mm in length, and were also formed into rotating bending fatigue test pieces 1 having a shape as shown in FIG 1.
- test spur gears 4 Normalized materials of 150 mm in diameter were machined into test spur gears 4 having a pitch radius of 54 mm, 27 teeth, a module of 4, a facewidth of 9 mm, a shaft hole radius of 35 mm (an equivalent round bar diameter of 10.5 mm ⁇ ) as shown in FIG 2.
- test pieces and the gears produced from Steels 11, 12 and 14 were subjected to low-pressure carburization (vacuum carburization) and gas quenching under the conditions of "Process 1" shown in Table 2.
- test pieces produced from Steel 13 were gas-carburized and oil-quenched under the conditions of "Process 2" shown in Table 3.
- the severity of quenching H after the carburization is 0.05 (cm -1 ) as shown in Table 2, and the elements of the production method of the present invention are included.
- test pieces prepared as described above were subjected to the following tests.
- a hardness distribution (internal hardness) of a cross section was investigated using a Vickers hardness meter.
- the surface layer hardness (surface hardness) of each carburized member was measured at a position of 0.02 mm from the surface.
- the troostite area rate was measured by image analysis of scanning electron micrographs.
- the surface carbon concentration was measured at a position of 50 ⁇ m from the surface via an X-ray macroanalyzer.
- the retained austenite area rate was measured at a surface of the member using a Co-K ⁇ ray in an X-ray diffraction apparatus.
- the surface residual stress was measured by a half value breadth midpoint method, using an Fe-K ⁇ ray in an X-ray stress meter.
- Process 1 Step Temperature Time Atmosphere Pressure Severity of Quenching H Carburizing 930°C 2 h Acetylene 20 mbar - Diffusion 930°C 1 h Acetylene 20 mbar - Thermal uniforming 850°C 0.5 h Acetylene 20 mbar - Quenching - - Nitrogen 8 bar 0.05 cm -1 Tempering 150°C 2 h Atmosphere Atmospheric - Process 2 Step Temperature Time Atmosphere Pressure Severity of Quenching H Carburizing 930°C 3 h Mixed gas of CO, H 2 , N 2 , etc.
- the specimen "Steel 13 + Process 2" had a lower surface layer hardness and a lower central portion hardness than any one of the specimens "Steel 11, 12 + Process 1".
- the specimen "Steel 14 + Process 1" had a surface layer hardness and a central portion hardness that are approximately equal to those of the specimens "Steel 11, 12 + Process 1", but had a greater retained austenite area rate and a smaller surface residual stress. Correspondingly, the member was inferior in the plane fatigue strength.
- the gear accuracy and the dimensional accuracy were evaluated as described below.
- Tooth space heights were measured all round the circumference of each gear, and a value obtained by subtracting a minimum value from a maximum value was determined as a tooth space runout.
- a ball was placed in two tooth spaces of gears facing each other, and an outer periphery thereof was measured via a dedicated OBD measuring device.
- OBD measurement circumferential directions were two perpendicular directions (X, Y), and upper, intermediate and lower sites (three sites) (A, B, C) were defined in the direction of facewidth, as indicated in FIGS. 2a and 2b.
- OBD ellipse an absolute value of the difference in OBD in the two perpendicular directions was determined.
- As an OBD taper a difference between an upper OBD and a lower OBD in the direction of facewidth was determined.
- the alloy steel it is appropriate to make a setting such that the alloy steel contains Fe as a main component and, as subsidiary components, 0.12 to 0.22 wt.% of C, 0.5 to 1.5 wt.% of Si, 0.25 to 0.45 wt.% of Mn, 0.5 to 1.5 wt.% ofNi, 1.3 to 2.3 wt.% of Cr, 0.001 to 0.003 wt.% of B, 0.02 to 0.06 wt.% of Ti, 0.02 to 0.12 wt.% ofNb, and 0.005 to 0.05 wt.% of Al.
- N 106 ⁇ C(wt.%) + 10.8 ⁇ Si(wt.%) + 19.9 ⁇ Mn(wt.%) + 16.7 ⁇ Ni(wt.%) + 8.55 ⁇ Cr(wt.%) + 45.5 ⁇ Mo(wt.%) + 28
- N is 87.6 and 93.4, respectively, whereas in Steel Grades 13, 14, not included in the present invention in terms of the ranges of components, N is greater than 95. If N is greater than 95, the hardness of the steel in the rolled state or the hardness of the steel in the normalized state remarkably increases, so that neither required machine workability nor required cold workability can be achieved. Therefore, if productivity is highly valued, it is necessary to control the composition of the steel so that the component parameter N is less than or equal to 95.
- the composition of the steel is set so that no ferrite is produced in a range of cooling rate greater than or equal to 12°C/sec. (hereinafter, referred to as "upper limit cooling rate), in order to ensure that the sufficient hardening of the carburized layer can be achieved even by gas cooling. If ferrite is produced although the cooling rate is greater than or equal to 12°C/sec., it is impossible to accomplish the sufficient production of martensite in the carburized layer by gas cooling, leading to insufficient hardness.
- the composition of the steel is set so that if the cooling rate is less than or equal to 0.1°C/sec., no bainite is produced. If bainite is produced even though the cooling rate is less than or equal to 0.1°C/sec., the hardening reaches the internal layer portion, which is not affected by the carburized layer. Thus, strain increases.
- the setting is made so that no bainite is produced if the cooling rate is less than 0.1°C/sec., production of bainite is sufficiently prevented or reduced in an actual range of annealing cooling rate, so that a highly workable structure with a large amount of ferrite and pearlite can be provided. Therefore, if the rate of cooling from austenite is within a range corresponding to the annealing state, that is, a state where the material is air-cooled or let stand to cool, the material is provided with a hardness that is sufficiently low to improve the workability. Thus, the working prior to the carburizing and quenching process becomes easier.
- an internal layer portion can be provided with a structure in which bainite is major if the cooling rate is set at 0.1 to 10°C/sec. It is particularly desirable to select such a composition that the cooling at 3°C/sec. will provide a structure mainly formed by bainite.
- steels indicated in Table 6 (Steels 21 to 24 and Steels 31 to 38) were melted and formed into ingots, which were bloom-rolled and bar-rolled to produce round bars of 70 mm in diameter.
- test pieces and the gears were processed separately by three different production methods (Processes 3 to 5).
- Process 3 is characterized by gas carburization and oil quenching.
- steel is carburized and quenched and then tempered in a carburizing gas atmosphere in the manner of heating at 930°C for 5 hours ⁇ diffusion at 850°C for 1 hour ⁇ oil-quenching at 130°C ⁇ tempering at 180°C for 1 hour.
- the severity of quenching H in this case is 0.15 (cm -1 ).
- Process 4" is characterized by vacuum carburization and gas cooling. In this process, steel is carburized and quenched and then tempered in the manner of heating at 930°C for 5 hours ⁇ diffusion at 850°C for 1 hour ⁇ nitrogen gas cooling ⁇ tempering at 180°C for 1 hour.
- the severity of quenching H in this case is 0.05 (cm -1 ).
- Process 5" is similar to Process 4, except that the nitrogen gas cooling in Process 4 is changed to oil quenching at 130°C.
- the severity of quenching H in this case is 0.15 (cm -1 ).
- test pieces and the gears processed by the above-described process were subjected to measurements, tests, and the like as in Example 1.
- Steel Grades 31 to 34 had a slack quenched structure due to intergranular oxidation formation at the time of gas carburization, and therefore exhibited low surface hardness and low strengths. Furthermore, since oil cooling causes rapider quenching and greater non-uniformity in cooling than gas cooling, the variation in precision due to hardening strain increased.
- each of Steel Grades 21 to 24 exhibited a high surface hardness and an appropriate value of internal hardness, and reduced strain. Thus, it is apparent that high strengths and low strains were achieved.
- this example also indicates that it is possible to increase the strength while sufficiently reducing the hardening strain in the members if a specific alloy steel having a C content, an Si content and hardenability J within the aforementioned specific ranges is used as a raw material, and is subjected to a carburizing process in an oxidation inhibitive atmosphere, thereby forming a carburized layer, and then the steel is quenched under the condition of the specific severity of quenching H.
- the alloy steel it is appropriate to make a setting such that the alloy steel contains Fe as a main component and, as subsidiary components, 0.1 to 0.5 wt.% of C, 0.5 to 1.0 wt.% of Si, 0.3 to 1.0 wt.% of Mn, 0.1 to 1.0 wt.% of Cr, 0.003 to 0.015 wt.% of P, 0.005 to 0.03 wt.% of S, 0.01 to 0 ⁇ 06 wt.% of Al, and 0.005 to 0.03 wt.% ofN, and at least one of 0.3 to 1.3 wt.% of Mo and 0.1 to 1.0 wt.% of Ni.
- at least one species selected from the group consisting of at most 0.01% by weigh of Ca, at most 0.01% by weight of Mg, at most 0.05% by weight ofZr and at most 0.1% by weight of Te may be contained.
Abstract
Provided are a carburized and hardened member that allows strength
enhancement while sufficiently reducing the hardening strain, without increasing the
production cost, and a production method for the carburized and hardened member.
An alloy steel which contains Fe as a main component and contains 0.10 to 0.50 wt.%
of C and 0.50 to 1.50 wt.% of Si and whose hardenability J based on an end quenching
test is in a range of 35 to 50 (at 12.5 mm) is used as a raw material. After the material
is formed into a member of a desired shape, a carburized layer is formed by performing
a carburizing process in an oxidation inhibitive atmosphere. After the carburizing
process, a quenching process is performed in a condition that cooling is monotonously
performed from a pearlite transformation point (A1 point) to a martensite
transformation start point (Ms point), and a condition that a severity of quenching H is
in a range of 0.01 to 0.08 (cm-1).
Description
The present invention relates to a carburized and hardened member that is
excellent in fatigue strength and dimensional accuracy, and a production method for the
member.
For example, for power transmission component parts of an automatic
transmission, for example, gears and the like, carburized and hardened members
subjected to a carburizing and quenching process are often used in order to increase the
surface hardness and the toughness.
Conventional carburized and hardened members are normally produced by
forming a case hardening steel (JIS: SCM420H, SCR420H, SNCM220) or the like
into a desired shape, and then gas-carburizing the steel in a carburizing atmosphere, and
then quenching it in an oil or the like.
As for the carburized and hardened members, cost cut and performance
improvement are demanded more strongly than ever.
In order to achieve both a cost cut and a performance improvement, it is
necessary to remove each of problems of the conventional carburized and hardened
members produced from a conventional case hardening steel by an ordinary carburizing
and quenching method.
One of goals regarding the carburized and hardened members is to further
improve the post-carburizing and quenching process strength and, at the same time,
improve the dimensional accuracy by reducing or suppressing the hardening strain.
However, improved hardenability normally leads to increased hardening strain,
as well known. There is a possibility that the strength prior to the carburizing and
quenching process may increase resulting in degraded processability and therefore
increased cost of processing.
The present invention has been accomplished in view of the aforementioned
problems of the conventional art. It is an object of the present invention to provide a
carburized and hardened member that allows strength enhancement while sufficiently
reducing the hardening strain, and a production method for the carburized and hardened
member.
A first aspect of the present invention is a carburized and hardened member
production method characterized in: that an alloy steel which contains Fe as a main
component and contains 0.10 to 0.50 wt.% of C and 0.50 to 1.50 wt.% of Si and whose
hardenability J based on an end quenching test is in a range of 35 to 50 (at 12.5 mm) is
used as a raw material; and that after the material is formed into a member of a desired
shape, a carburized layer is formed by performing a carburizing process in an oxidation
inhibitive atmosphere; and that after the carburizing process, a quenching process is
performed in such a condition that cooling is monotonously performed from a pearlite
transformation point (A1 point) to a martensite transformation start point (Ms point),
and such a condition that a severity of quenching H is in a range of 0.01 to 0.08 (cm-1).
The aforementioned hardenability J based on an end quenching test is a value
acquired by an end quenching test method prescribed in JIS: G0561 (generally termed
"Jominy end quench test method"). Furthermore, the indication of (at 12.5 mm)
means that the value of hardenability J is a value of hardenability J regarding a position
of 12.5 mm from the water cool-side end surface of a rod-like test piece in the Jominy
end quench test method.
The aforementioned severity of quenching H is a widely used index espoused
by Grossmann et al. to indicate the strength of quenching, and is defined as in
H=0.5×(α/γ) where γ is the heat conductivity (kcal/mh°C) of a steel to be processed, and
α is a surface heat transfer factor (kcal/mh2°C) of the steel in a hardening atmosphere.
In the present invention, a specific alloy of which
the C content and the Si content and the hardenability J are within the specific ranges is
used as a raw material. After a carburized layer is formed by performing the
carburizing process in the oxidation inhibitive atmosphere, the quenching process is
performed so as to fulfill the aforementioned conditions of monotonous cooling and the
aforementioned condition of specific severity of quenching H. That is, only after the
material characteristics and the production conditions are fulfilled, it becomes possible
to provide a carburized and hardened member in which the strength is enhanced while
the hardening strain is sufficiently reduced.
This will be further explained. The setting of the C content within the range
of 0.1 to 0.50 wt.% makes it possible to secure an appropriate toughness and an
appropriate strength of a non-carburized portion (internal portion) after the carburizing
and quenching process. If the C content is less than 0.1 wt.%, the aforementioned
effect is not sufficient. If the C content exceeds 0.50 wt.%, the pre-quenching
hardness becomes excessively high, thus creating a possibility of increased processing
cost and reduced toughness. Furthermore, due to increased structural transformation
rate of the interior of the non-carburized portion following the carburizing and
quenching process, transformation stress increases, and due to great quenching strain,
the component part accuracy may degrade.
Furthermore, in the present invention, the member positively contains Si as a
component, and the content thereof is 0.50 to 1.50 wt.%. The carburizing process is
performed in an oxidation inhibitive atmosphere. Therefore, it becomes possible to
achieve improved plane fatigue strength, improved hardenability, improved resistance to
temper softening, etc. while reducing the intergranular oxidation, which is likely to
occur at the time of the carburizing process.
If the Si content is less than 0.50 wt.%, the aforementioned improvement effect is
small; in particular, there is a problem of reduction of intergranular oxidation
preventative effect at the time of the carburizing process. Conversely, if the Si content
is greater than 1.50 wt.%, the improvement effect becomes saturated, and uniform
austenitization prior to quenching is difficult. In order to prevent or curb degradations
in the plastic processability, the cutting processability and the formability of the material,
it is preferable that the Si content be less than or equal to 0.70 wt.%. Therefore, a
preferable range of the Si content is a range greater than 0.50 wt.% and less than or
equal to 0.70 wt.%.
The hardenability J of the material is limited within the range of 35 to 50 (at
12.5 mm). Therefore, excellent hardening effect can be achieved even if the range of
the severity of quenching H is limited to the aforementioned range. If the
hardenability J is less than 35, it becomes impossible to achieve sufficient hardening
effect on the carburized layer and the non-carburized portion (internal portion) in the
quenching process following the carburizing process, and it is therefore impossible to
achieve a desired strength enhancement. Therefore, it is preferable that the
hardenability J be greater than or equal to 38. If the hardenability J exceeds 50, the
structural transformation rate of the internal portion, that is, the non-carburized portion,
rises, so that the transformation stress increases and the hardening strain becomes more
likely. If the hardenability J is higher, the hardness prior to the carburizing and
quenching process is correspondingly higher, so that processability, such as the plastic
processability prior to the carburizing process, the cutting processability, etc., degrades.
Therefore, in order to prevent such degradation of workability, it is preferable that
hardenability J be less than or equal to 45.
The severity of quenching H is limited within the range of 0.01 to 0.08 (cm-1).
If the alloy having the specific amount of carbon and having the hardenability is used, it
becomes possible to substantially prevent or reduce the hardenability strain at the time
of hardening process and therefore secure excellent dimensional accuracy.
If the severity of quenching H is less than 0.01 (cm-1), it is impossible to achieve
sufficient hardening effect on the carburized layer and the non-carburized portion
(internal portion) in a hardening process following the carburizing process as in the case
where the hardenability J is less than 35. Therefore, desired strength enhancement
cannot be accomplished. If the severity of quenching H is greater than 0.08 (cm-1), the
transformation stress increases due to, particularly, increased structural transformation
rate of the internal portion, that is, the non-carburized portion, and therefore the
hardening strain is likely to occur, as in the case where the hardenability J is greater than
50.
The quenching process is performed under the condition that the cooling
monotonously occurs from the A1 point to the Ms point, in addition to the condition of
the range of severity of quenching H. The term "monotonously" herein means that
re-heating is not performed during the cooling process, that is, there is no rise of the
material temperature during the cooling. Therefore, examples of the case where the
condition of monotonous cooling is fulfilled include a case where the material
temperature continues to fall, and a case where if the temperature stops falling during
the process, the temperature remains constant and never rises, and then starts falling
again. Furthermore, changes in the cooling rate are allowable.
As the monotonous cooling is adopted as an essential condition, precipitation
of carbides can be substantially prevented or reduced.
With regard to the monotonous cooling condition, it is possible to select a
cooling condition such that the cooling does not enter a region of a nose of an S curve
indicated in an isothermal transformation diagram within the carburized portion. This
selection secures sufficient martensite transformation.
Although this may be a repeated statement, the present invention provides a
carburized and hardened member in which the strength is enhanced while the hardening
strain is sufficiently reduced, as the invention comprises the aforementioned C content,
the Si content, the hardenability J, the carburizing process in an oxidation inhibitive
atmosphere, and the quenching process that fulfills the condition of the monotonous
cooling and the condition of the specific severity of quenching H. If any one of these
elements is absent, the intended object cannot be achieved. The present inventors have
discovered this through many experiments.
A second aspect of the present invention is a carburized and hardened member
produced by the above-described production method, characterized in that a surface
hardness of the carburized layer is in a range of 700 to 900 Hv, and an internal hardness
of a non-carburized portion located inward of the carburized layer is in a range of 250 to
450 Hv.
This carburized and hardened member is produced by adopting the
above-described production method and by adjusting the component range processing
condition so as to restrict the surface hardness of the carburized layer and the internal
hardness of the non-carburized portion within the aforementioned ranges. Therefore, it
becomes possible to secure a static strength (tensile strength, flexural strength, torsional
strength, etc.) and a dynamic strength (plane fatigue strength, bending fatigue strength,
torsion fatigue strength, etc.) in a region from the surface to the internal portion (core
portion), with respect to the distribution of stress applied to the member which results
from the operating stress caused on the member by load applied to the member and the
stress concentrated adjacent to the surface of the member due to bumps and dips, holes,
etc. of the member.
If the surface hardness of the carburized layer is less than 700 Hv, a
conceivable problem is that strength cannot be secure corresponding to the stress
concentration adjacent to the surfaces of the member. Another conceivable problem is
insufficient abrasion resistance in outermost surface. If the surface hardness is greater
than 900 Hv, production of carbide, such as cementite and the like, in the surface layer
is conceivable. Therefore, a conceivable problem is insufficient strength and, more
particularly, reduced toughness.
If the internal hardness of the non-carburized portion is less than 250 Hv, the
problem of insufficient strength and, more particularly, insufficient static strength, can
be considered. If the internal hardness is greater than 450 Hv, the following problem is
possible, taking the rate of transformation of structure into consideration. That is,
when a hardening process is performed so as to secure 450 Hv, a great transformation
stress occurs, which causes a great hardening strain and therefore makes a factor of
degradation in component parts accuracy.
In the production method for a carburized and hardened member according to
the first aspect of the present invention, it is preferable that the carburizing process be
performed in a reduced-pressure atmosphere having a reduced pressure of 1 to 30 hPa.
Therefore, it becomes possible to easily provide the oxidation inhibitive atmosphere
through pressure reduction, and therefore sufficiently prevent intergranular oxidation at
the time of carburization. The value of the reduced pressure of the reduced-pressure
atmosphere being less than 1 hPa is excessive for substantial prevention of oxidation.
If such value of the reduced pressure is required, the device for the pressure reduction
needs to have high capability for pressure reduction, and creates a problem of cost
increase. If the value of the reduced pressure is higher than 30 hPa, the oxidation
preventing effect degrades, and furthermore, other problems, such as production of soot
in the carburizing furnace, and the like, occur.
It is also preferable that the carburizing process be performed in an atmosphere
containing an inert gas as a main component. This also makes it possible to easily
form the oxidation inhibitive atmosphere. Examples of the inert gas include nitrogen
gas, argon gas, etc.
It is also preferable that the carburizing process be performed so that a surface
carbon amount in the carburized layer becomes 0.6 to 1.5 wt.% (claim 4). The surface
carbon concentration in the carburized layer affects the surface hardness of the
carburized and hardened member. If the surface carbon amount in the carburized layer
is less than 0.6 wt.%, there occurs a problem of insufficient surface hardness. If the
surface carbon amount is greater than 1.5 wt.%, the precipitation of carbide becomes
great so that the hardenability of the base remarkably degrades and the surface hardness
becomes insufficient.
It is also preferable that intergranular oxidation progressing from a surface of
the raw material be at most 3 µm. That is, it is preferable to restrict the intergranular
oxidation to 3 µm or less from the surface by adjusting the oxidation inhibitive
atmosphere, the heating temperature, the heating time, etc., at the time of carburization.
The intergranular strength decreases if an intergranular oxide (portion) is
produced. Therefore, if intergranular oxidation reaches a depth beyond 3 µm, there is
a danger of reduced abrasion resistance due to insufficient strength of the member,
reduced hardness, etc. Furthermore, at the time of intergranular oxidation, surrounding
alloy elements are also taken up into the intergranular oxide due to chemical reactions.
Therefore, the hardenability-improving elements in the carburized and hardened layer
around intergranular oxides are taken up and consumed by the intergranular oxides,
thereby forming regions where additives are depleted, around the intergranular oxide
layer. Therefore, the hardenability of the carburized and hardened layer becomes
insufficient. Hence, there is a danger of causing insufficient hardness and insufficient
strength.
It is also preferable that the raw material have a surface compression residual
stress of 300 to 800 MPa. That is, it is preferable to set the surface compression
residual stress to at least 300 MPa by adjusting the composition of the raw material, the
oxidation inhibitive atmosphere for the carburization, the heating temperature, the
heating time, etc. Therefore, the tensile stress near the surface can be reduced by the
compression residual stress near the surface of the member. In particular, the dynamic
strength (planer fatigue strength, bending fatigue strength, torsional fatigue strength)
can be improved. If the surface compression residual stress is greater than 800 MPa, it
is necessary to increase the cooling rate during the quenching process beyond a limit in
order to increase the amount of martensite. Therefore, great hardening strain occurs,
and therefore a dimensional accuracy of the member cannot be secured.
The surface compression residual stress can be produced by forming the
martensite via the quenching process of the carburized layer, and creating a compression
stress field due to volume expansion involved in the transformation. However, if the
amount of martensite produced is small, that is, if the amount of retained austenite is
great, or if the troostite structure is great in amount, it is impossible to form a sufficient
compression residual stress field. Therefore, the reduction of the retained austenite
(specifically, to 25% or less) and the reduction of the troostite structure (specifically, to
10% or less) are effective in view of enhancement of compression residual stress effect.
The absorption of volume expansion at the time of martensite transformation does not
considerably contribute to enhancement of the surface compression residual stress if the
amount of martensite is small. If the amount of martensite is small, plastic
deformation of the surrounding retained austenite or troostite structure is involved, and
therefore stress reduces. However, if the amount of martensite increases and the
retained austenite or troostite structure reduces in amount as mentioned above, the
density of dislocation introduced by plastic deformation increases, so that slip is
restrained. Therefore, the surface compression residual stress rapidly increases.
In another possible method, the compression residual stress can be increased by
performing a surface process, such as shot peening, after the quenching process. In the
latter method, turning the retained austenite into martensite by the shot peening process
is more advantageous in increasing the compression residual stress.
It is also preferable that in the quenching process, quenching be performed
with the severity of quenching H being in said range during a transition from a
temperature in an austenite region to 300°C. Therefore, sufficient quenching effect
can be achieved. If the severity of quenching H in a cooling process from the
temperature of the austenite region to 300°C is less than 0.01 (cm-1), the quenching will
be insufficient. Thus, desired hardened structure and characteristic cannot be achieved,
and the strength of the member will be insufficient. If the severity of quenching H in a
cooling process from the temperature of the austenite region to 300°C is greater than
0.08 (cm-1), the quenching will be excessive, so that the structure transformation stress
and the thermal stress will increase. Therefore, there is a possibility of increased
hardening strain and degraded component part accuracy.
It is also preferable that in the quenching process, quenching be accomplished
by gas cooling. Therefore, it becomes relatively easy to secure the aforementioned
severity of quenching H.
It is also preferable that the quenching by gas cooling use an inert gas.
Therefore, a safety can be secured during the quenching.
It is also preferable that the inert gas be a nitrogen gas. The adoption of
nitrogen gas as the aforementioned inert gas is preferable in view of cost, ease of
handling, availability at the time of mass-production operation, etc.
In the carburized and hardened member of the second aspect of the present
invention, a retained austenite area rate of the carburized layer preferably is at most
25%. If the retained austenite area rate is greater than 25%, structural transformation
from retained austenite into martensite occurs in association with changes in
temperature and operating stress during a working process after the carburizing and
quenching process, or during the use of the member. Due to the stress of the
transformation, strain occurs, and the component parts accuracy will likely degrade. It
is more preferable that the retained austenite area rate be 20% or less. The retained
austenite area rate can be reduced by other manners. For example, the area rate can be
reduced by forcibly turning the retained austenite into martensite via shot peening or the
like.
It is also preferable that a troostite structure area rate of a surface layer of the
carburized layer be at most 10%. The troostite is a slack-quenched structure formed in
the carburized layer after the carburizing and quenching process, and has a low hardness.
Therefore, if the troostite structure area rate is greater than 10%, low-strength troostite
will reduce the strength of the component part.
It is also preferable that an internal structure of the carburized and hardened
member be bainite. More specifically, it is desirable that the area rate of bainite in a
sectional structure be at least 50%. Unlike the case of martensite, transformation of
bainite progresses while iron atoms forming a lattice partially diffuse. Therefore, the
strain associated with transformation is less in bainite than in martensite. Furthermore,
bainite has a greater hardness than pearlite, which is produced if the cooling rate is
lower. Thus, bainite appropriately enhances the strength of the internal non-carburized
layer. In order to form an internal layer portion mainly from bainite, it is desirable to
select such a composition as to form a structure mainly from bainite by setting the
severity of quenching H within the range of 0.01 to 0.08 (cm-1). Therefore, it becomes
possible to provide a component part that has high strength and high toughness.
It is also preferable that the carburized and hardened member be a carburized
toothed gear. The toothed gears require various strict conditions. The excellent
characteristics achieved by the above-described production method are very effective
for the toothed gears.
The carburized and hardened members according to embodiments of the
present invention will be described in detail with reference to specific examples.
As Example 1, results of experiments conducted to verify advantages of the
present invention will be described.
Steels (Steel 11 to Steel 14) having chemical compositions shown in Table 1,
after being melt-formed in an arc furnace, were hot-rolled into round bars having a
diameter of 150 mm and a diameter of 32 mm. The round bars were normalized by
keeping them at 925°C for an hour and then air-cooling them.
Steel 11 and Steel 12 are steel grades having new compositions developed in
the example. Steel 13 and Steel 14 are steel grades corresponding to case hardening
steels SCM420 and SNCM 815 according to JIS.
Firstly, for each steel grade, a hardenability J was determined by conducting a
Jominy end quenching method according to JIS: G0561.
Results are shown in Table 1. This characteristic is a characteristic of a raw
material irrelevant to the production method described below.
Steel grade | Component element (wt%) | Hardenability J | |||||||||||
C | Si | Mn | S | Ni | Cr | Mo | B | Ti | Mb | A1 | N | ||
11 | 0.16 | 0.56 | 0.38 | 0.012 | 0.96 | 1.47 | 0.01 | 0.0022 | 0.044 | 0.05 | 0.013 | 0.006 | 38 |
12 | 0.18 | 0.75 | 0.35 | 0.009 | 0.71 | 2.22 | 0.01 | 0.0018 | 0.035 | 0.03 | 0.019 | 0.005 | 42 |
13 | 0.2 | 0.21 | 0.78 | 0.011 | 0.02 | 1.01 | 0.17 | - | - | - | 0.027 | 0.015 | 25 |
14 | 0.15 | 0.25 | 0.47 | 0.009 | 4.34 | 0.83 | 0.27 | - | - | - | 0.04 | 0.018 | 37 |
As can be understood from Table 1, Steels 11 and 12 are alloy steels that are
applicable as a raw material in the present invention in view of material quality and
hardenability J. However, as for Steel 13, the hardenability J and the Si content are
outside their respective ranges according to the present invention. As for Steel 14, the
Si content is outside the range according the present invention.
Steels 11 to 14 were formed into round bar test pieces (not shown) of 25 mm in
diameter and 50 mm in length, and were also formed into rotating bending fatigue test
pieces 1 having a shape as shown in FIG 1.
Normalized materials of 150 mm in diameter were machined into test spur
gears 4 having a pitch radius of 54 mm, 27 teeth, a module of 4, a facewidth of 9 mm, a
shaft hole radius of 35 mm (an equivalent round bar diameter of 10.5 mm) as shown in
FIG 2.
The test pieces and the gears produced from Steels 11, 12 and 14 were
subjected to low-pressure carburization (vacuum carburization) and gas quenching
under the conditions of "Process 1" shown in Table 2.
The test pieces produced from Steel 13 were gas-carburized and oil-quenched
under the conditions of "Process 2" shown in Table 3.
In the aforementioned "Process 1", the severity of quenching H after the
carburization is 0.05 (cm-1) as shown in Table 2, and the elements of the production
method of the present invention are included.
In the aforementioned "Process 2", the severity of quenching H after the
carburization is 0.15 (cm-1) as shown in Table 3, and the elements of the production
method of the present invention are included.
The test pieces prepared as described above were subjected to the following
tests.
First, with regard to the round bar test pieces of 25 mm in diameter, a hardness
distribution (internal hardness) of a cross section was investigated using a Vickers
hardness meter. The surface layer hardness (surface hardness) of each carburized
member was measured at a position of 0.02 mm from the surface. Furthermore, at an
equivalent position, the troostite area rate was measured by image analysis of scanning
electron micrographs.
As for the intergranular oxidation layer, a greatest depth of the oxidation layer
from the superficial metallographic structure was measured by an optical microscope.
The surface carbon concentration was measured at a position of 50 µm from
the surface via an X-ray macroanalyzer.
The retained austenite area rate was measured at a surface of the member using
a Co-Kα ray in an X-ray diffraction apparatus.
The surface residual stress was measured by a half value breadth midpoint
method, using an Fe-Kα ray in an X-ray stress meter.
Measurement results are shown in Table 4.
| |||||
Step | Temperature | Time | Atmosphere | Pressure | Severity of Quenching H |
Carburizing | 930°C | 2 h | Acetylene | 20 mbar | - |
Diffusion | 930°C | 1 h | Acetylene | 20 mbar | - |
Thermal uniforming | 850°C | 0.5 h | Acetylene | 20 mbar | - |
Quenching | - | - | Nitrogen | 8 bar | 0.05 cm-1 |
Tempering | 150°C | 2 h | Atmosphere | Atmospheric | - |
Process 2 | |||||
Step | Temperature | Time | Atmosphere | Pressure | Severity of Quenching H |
Carburizing | 930°C | 3 h | Mixed gas of CO, H2, N2, etc. formed by reaction of butane and air | Atmospheric spheric | - |
Diffusion | 930°C | 1 h | Mixed gas of CO, H2, N2, etc. formed by reaction of butane and air | Atmospheric spheric | - |
Thermal uniforming | 850°C | 0.5 h | Mixed gas of CO, H2, N2, etc. formed by reaction of butane and air | Atmospheric | - |
Quenching | 120°C | - | Oil | Atmospheric | 0.15 cm-1 |
Tempering | 150°C | 2 h | Atmosphere | Atmospheric | - |
As shown in Table 4, all the carburized and hardened specimens "Steel 11, 12 +
Process 1" produced from Steels 11 and 12 by Process 1 (hereinafter, combinations of
the steel grade and the production process will be indicated in the fashion of "Steel
Grade + Process") had a central portion hardness above 250 Hv. The structures in a
surface layer and a central portion were martensite, and no remarkable slack-quenched
structure existed.
In contrast, the specimen "Steel 13 + Process 2" had a lower surface layer
hardness and a lower central portion hardness than any one of the specimens "Steel 11,
12 + Process 1".
The specimen "Steel 14 + Process 1" had a surface layer hardness and a central
portion hardness that are approximately equal to those of the specimens "Steel 11, 12 +
Process 1", but had a greater retained austenite area rate and a smaller surface residual
stress. Correspondingly, the member was inferior in the plane fatigue strength.
As for the rotating bending fatigue test, an Ono-type rotary bending fatigue
testing machine was used to determine fatigue strengths with the reference number of
repetitions being ten millions. Results are shown as the bending fatigue and the plane
fatigue in Table 4.
As can be understood from Table 4, the specimens "Steel 11, 12 + Process 1"
achieved considerably better characteristics in the rotating bending fatigue strength than
the specimens "Steel 13 + Process 2" and "Steel 14 + Process 1".
As for the gears, the gear accuracy and the dimensional accuracy were
evaluated as described below.
To evaluate the gear accuracy, an amount of error in directions of gear pressure
and an amount of error in the direction of helix angle were measured on each of the
right and left tooth flanks, via a dedicated precision gear accuracy measuring machine.
Tooth space heights were measured all round the circumference of each gear, and a
value obtained by subtracting a minimum value from a maximum value was determined
as a tooth space runout.
To evaluate the dimensional accuracy, a ball was placed in two tooth spaces of
gears facing each other, and an outer periphery thereof was measured via a dedicated
OBD measuring device. As for the OBD measurement, circumferential directions
were two perpendicular directions (X, Y), and upper, intermediate and lower sites (three
sites) (A, B, C) were defined in the direction of facewidth, as indicated in FIGS. 2a and
2b. As an OBD ellipse, an absolute value of the difference in OBD in the two
perpendicular directions was determined. As an OBD taper, a difference between an
upper OBD and a lower OBD in the direction of facewidth was determined.
Results are shown in FIG 5.
Steel grade | Carburizing and quenching step | Gear accuracy (%) | Dimensional accuracy (%) | |||||
flank Tooth | Variation in characteristics | Tooth space runout | OBD variation | OBD ellipse | OBD taper | |||
Pressure angle error | Helix angle error | |||||||
11 | | Right | 45 | 51 | 68 | 70 | 82 | 35 |
Left | 48 | 49 | ||||||
12 | | Right | 62 | 65 | 73 | 78 | 81 | 40 |
Left | 58 | 60 | ||||||
13 | Process 2 | Right | 100 | 100 | 100 | 100 | 100 | 100 |
Left | 100 | 100 | ||||||
14 | | Right | 47 | 48 | 70 | 65 | 80 | 30 |
Left | 50 | 55 |
As can be understood from Table 5, the specimens "Steel 11, 12 + Process 1"
exhibited better gear accuracies and better dimensional accuracies than the other
members.
The aforementioned results indicate that it is possible to increase the strength
while sufficiently reducing the hardening strain in the specimens "Steel 11, 12 + Process
1" in which a specific alloy steel having a C content, an Si content and hardenability J
within the aforementioned specific ranges was used as a raw material, and was
subjected to a carburizing process in an oxidation inhibitive atmosphere, thereby
forming a carburized layer, and then the steel was quenched under the condition of the
specific severity of quenching H.
As for the alloy steel, it is appropriate to make a setting such that the alloy steel
contains Fe as a main component and, as subsidiary components, 0.12 to 0.22 wt.% of C,
0.5 to 1.5 wt.% of Si, 0.25 to 0.45 wt.% of Mn, 0.5 to 1.5 wt.% ofNi, 1.3 to 2.3 wt.% of
Cr, 0.001 to 0.003 wt.% of B, 0.02 to 0.06 wt.% of Ti, 0.02 to 0.12 wt.% ofNb, and
0.005 to 0.05 wt.% of Al.
More specifically, it is appropriate to prepare a composition such that a
component parameter N defined as below is 95 or less.
N ≡ 106×C(wt.%) + 10.8×Si(wt.%) + 19.9×Mn(wt.%) + 16.7×Ni(wt.%) +
8.55×Cr(wt.%) + 45.5×Mo(wt.%) + 28
In Steel Grades 11, 12, N is 87.6 and 93.4, respectively, whereas in Steel
Grades 13, 14, not included in the present invention in terms of the ranges of
components, N is greater than 95. If N is greater than 95, the hardness of the steel in
the rolled state or the hardness of the steel in the normalized state remarkably increases,
so that neither required machine workability nor required cold workability can be
achieved. Therefore, if productivity is highly valued, it is necessary to control the
composition of the steel so that the component parameter N is less than or equal to 95.
In the alloy steel satisfying the component ranges according to the present
invention, no bainite is produced if the cooling rate is equal to or less than 0.1°C/sec.,
and no ferrite is produced if the cooling rate is greater than or equal to 12°C/sec.
These ranges of the cooling rate can be specified through measurements of continuous
cooling transformation diagrams (CCT diagrams) of a steel at various cooling rates.
In the present invention, the composition of the steel is set so that no ferrite is
produced in a range of cooling rate greater than or equal to 12°C/sec. (hereinafter,
referred to as "upper limit cooling rate), in order to ensure that the sufficient hardening
of the carburized layer can be achieved even by gas cooling. If ferrite is produced
although the cooling rate is greater than or equal to 12°C/sec., it is impossible to
accomplish the sufficient production of martensite in the carburized layer by gas cooling,
leading to insufficient hardness.
However, excessively high hardenability is disadvantageous, too. That is, if
martensite is excessively produced in the internal layer portion where the carburization
does not have effect, the production of martensite in the entire member becomes
considerably great, leading to degraded dimensional accuracy. Therefore, it is
important to select a composition so that at the time of gas quenching, martensite is
sufficiently produced in the carburized layer whereas martensite is not excessively
produced in the internal layer portion. Specifically, the composition of the steel is set
so that if the cooling rate is less than or equal to 0.1°C/sec., no bainite is produced. If
bainite is produced even though the cooling rate is less than or equal to 0.1°C/sec., the
hardening reaches the internal layer portion, which is not affected by the carburized
layer. Thus, strain increases.
If the setting is made so that no bainite is produced if the cooling rate is less
than 0.1°C/sec., production of bainite is sufficiently prevented or reduced in an actual
range of annealing cooling rate, so that a highly workable structure with a large amount
of ferrite and pearlite can be provided. Therefore, if the rate of cooling from austenite
is within a range corresponding to the annealing state, that is, a state where the material
is air-cooled or let stand to cool, the material is provided with a hardness that is
sufficiently low to improve the workability. Thus, the working prior to the carburizing
and quenching process becomes easier.
Furthermore, it is desirable to select such a composition that an internal layer
portion can be provided with a structure in which bainite is major if the cooling rate is
set at 0.1 to 10°C/sec. It is particularly desirable to select such a composition that the
cooling at 3°C/sec. will provide a structure mainly formed by bainite.
In this example, steels indicated in Table 6 (Steels 21 to 24 and Steels 31 to 38)
were melted and formed into ingots, which were bloom-rolled and bar-rolled to produce
round bars of 70 mm in diameter.
Subsequently, the round bars of 70 mm were stretched to 120 mm by hot
forging. After being normalized at 925°C, the materials were formed into test pieces
and toothed gears as in Example 1 (see FIGS. 1 and 2).
The test pieces and the gears were processed separately by three different
production methods (Processes 3 to 5).
"Process 3" is characterized by gas carburization and oil quenching. In this
process, steel is carburized and quenched and then tempered in a carburizing gas
atmosphere in the manner of heating at 930°C for 5 hours→diffusion at 850°C for 1
hour→oil-quenching at 130°C→tempering at 180°C for 1 hour. The severity of
quenching H in this case is 0.15 (cm-1).
"Process 4" is characterized by vacuum carburization and gas cooling. In this
process, steel is carburized and quenched and then tempered in the manner of heating at
930°C for 5 hours→diffusion at 850°C for 1 hour→nitrogen gas cooling→tempering at
180°C for 1 hour. The severity of quenching H in this case is 0.05 (cm-1).
"Process 5" is similar to Process 4, except that the nitrogen gas cooling in
Process 4 is changed to oil quenching at 130°C. The severity of quenching H in this
case is 0.15 (cm-1).
The test pieces and the gears processed by the above-described process were
subjected to measurements, tests, and the like as in Example 1.
Results are shown in Tables 7 and 8.
As shown in Tables 7 and 8, Steel Grades 31 to 38 were inferior in the bending
fatigue strength and the plane fatigue strength; furthermore, the oil-cooled component
parts had great variation in precision due to hardening strain, and therefore would have
problems in practical use.
Steel Grades 31 to 34 had a slack quenched structure due to intergranular
oxidation formation at the time of gas carburization, and therefore exhibited low surface
hardness and low strengths. Furthermore, since oil cooling causes rapider quenching
and greater non-uniformity in cooling than gas cooling, the variation in precision due to
hardening strain increased.
In Steel Grades 37, 38, the quenching by oil-cooling was excessively strong
with respect to the hardenability of the steel materials, so that the internal hardness
excessively increased. The difference between the proportion of the surface structure
transformation and the proportion of the internal structure transformation was relatively
small, that is, the difference between the surface hardness and the internal hardness was
relatively small. Therefore, the surface layer residual stress was relatively small, and
the strengths were relatively low. Furthermore, since oil cooling causes rapider
quenching and greater cooling non-uniformity than gas cooling, the variation in
precision due to hardening strain increased.
In contrast, each of Steel Grades 21 to 24 exhibited a high surface hardness and
an appropriate value of internal hardness, and reduced strain. Thus, it is apparent that
high strengths and low strains were achieved.
Therefore, this example also indicates that it is possible to increase the strength
while sufficiently reducing the hardening strain in the members if a specific alloy steel
having a C content, an Si content and hardenability J within the aforementioned specific
ranges is used as a raw material, and is subjected to a carburizing process in an
oxidation inhibitive atmosphere, thereby forming a carburized layer, and then the steel
is quenched under the condition of the specific severity of quenching H.
As for the alloy steel, it is appropriate to make a setting such that the alloy steel
contains Fe as a main component and, as subsidiary components, 0.1 to 0.5 wt.% of C,
0.5 to 1.0 wt.% of Si, 0.3 to 1.0 wt.% of Mn, 0.1 to 1.0 wt.% of Cr, 0.003 to 0.015 wt.%
of P, 0.005 to 0.03 wt.% of S, 0.01 to 0·06 wt.% of Al, and 0.005 to 0.03 wt.% ofN,
and at least one of 0.3 to 1.3 wt.% of Mo and 0.1 to 1.0 wt.% of Ni. It is also possible
to contain, as subsidiary components, at least one of 0.05 to 1.5 wt.% of V, 0.02 to 0.2
wt.% ofNb, 0.01 to 0.2 wt.% ofTi, or 0.0005 to 0.005 wt.% ofB and 0.005 to 0.1 wt.%
of Ti, or 0.0005 to 0.005 wt.% of B and 0.11 to 0.2 wt.% of Ti. As still other elements,
at least one species selected from the group consisting of at most 0.01% by weigh of Ca,
at most 0.01% by weight of Mg, at most 0.05% by weight ofZr and at most 0.1% by
weight of Te may be contained.
Steel grade | Carburizing and quenching step | Gear accuracy (%) | Dimensional accuracy (%) | |||||
Tooth flank | Variation in characteristics | Tooth space runout | OBD variation | OBD ellipse | OBD taper | |||
pressure angel error | Helix angle error. | |||||||
21 | (Process 4) vacuum carburizing + gas cooling | Right | 48 | 60 | 65 | 55 | 80 | 36 |
Left | 52 | 54 | ||||||
22 | Right | 47 | 55 | 70 | 68 | 85 | 48 | |
Left | 48 | 59 | ||||||
23 | Right | 60 | 67 | 66 | 70 | 77 | 32 | |
Left | 52 | 61 | ||||||
27 | Right | 51 | 56 | 64 | 60 | 79 | 47 | |
Left | 47 | 52 | ||||||
31 | (Process 3) gas carburizing + oil cooling | Right | 103 | 108 | 105 | 98 | 100 | 110 |
Left | 112 | 105 | ||||||
32 | Right | 99 | 105 | 100 | 100 | 110 | 105 | |
Left | 18 | 98 | ||||||
33 | Right | 110 | 105 | 101 | 108 | 106 | 99 | |
Left | 105 | 104 | ||||||
34 | Right | 102 | 109 | 106 | 111 | 111 | 107 | |
Left | 106 | 110 | ||||||
35 | (Process 4) vacuum carburizing + gas cooling | Right | 60 | 59 | 70 | 65 | 77 | 43 |
Left | 51 | 65 | ||||||
Right | 59 | 55 | 78 | 64 | 85 | 48 | ||
36 | Left | 54 | 59 | |||||
37 | (Process 5) vacuum carburizing + oil cooling | Right | 99 | 106 | 105 | 97 | 110 | 102 |
Left | 108 | 111 | ||||||
38 | Right | 100 | 100 | 100 | 100 | 100 | 100 | |
Left | 100 | 100 |
Claims (15)
- A carburized and hardened member production method characterized in:that an alloy steel which contains Fe as a main component and contains 0.10 to 0.50 wt.% of C and 0.50 to 1.50 wt.% of Si and whose hardenability J based on an end quenching test is in a range of 35 to 50 (at 12.5 mm) is used as a raw material; andthat after the material is formed into a member of a desired shape, a carburized layer is formed by performing a carburizing process in an oxidation inhibitive atmosphere; andthat after the carburizing process, a quenching process is performed in a condition that cooling is monotonously performed from a pearlite transformation point (A1 point) to a martensite transformation start point (Ms point), and a condition that a severity of quenching H is in a range of 0.01 to 0.08 (cm-1).
- The carburized and hardened member production method according to claim 1, characterized in that the carburizing process is performed in a reduced-pressure atmosphere having a reduced pressure of 1 to 30 hPa.
- The carburized and hardened member production method according to claim 1, characterized in that the carburizing process is performed in an atmosphere containing an inert gas as a main component.
- The carburized and hardened member production method according to claim 1, characterized in that the carburizing process is performed so that a surface carbon amount in the carburized layer becomes 0.6 to 1.5 wt.%.
- The carburized and hardened member production method according to claim 1, characterized in that intergranular oxidation progressing from a surface of the raw material is at most 3 µm.
- The carburized and hardened member production method according to claim 1, characterized in that the raw material has a surface compression residual stress of 300 to 800 MPa.
- The carburized and hardened member production method according to claim 1, characterized in that in the quenching process, quenching is performed with the severity of quenching H being in said range during a transition from a temperature in an austenite region to 300°C.
- The carburized and hardened member production method according to claim 1, characterized in that in the quenching process, quenching is accomplished by gas cooling.
- The carburized and hardened member production method according to claim 8, characterized in that the quenching accomplished by the gas cooling uses an inert gas.
- The carburized and hardened member production method according to claim 9, characterized in that the inert gas is a nitrogen gas.
- A carburized and hardened member produced by a production method described in claim 1, characterized in that a surface hardness of the carburized layer is in a range of 700 to 900 Hv, and an internal hardness of a non-carburized portion located inward of the carburized layer is in a range of 250 to 450 Hv.
- The carburized and hardened member according to claim 11, characterized in that a retained austenite area rate of the carburized layer is at most 25%.
- The carburized and hardened member according to claim 11, characterized in that a troostite structure area rate of a surface layer of the carburized layer is at most 10%.
- The carburized and hardened member according to claim 11, characterized in that an internal structure of the carburized and hardened member is bainite.
- The carburized and hardened member according to claim 11, characterized in that the carburized and hardened member is a carburized toothed gear.
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2001392410 | 2001-12-25 | ||
JP2001392410 | 2001-12-25 | ||
PCT/JP2002/013561 WO2003056054A1 (en) | 2001-12-25 | 2002-12-25 | Carburized and quenched member and method for production thereof |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1550736A1 true EP1550736A1 (en) | 2005-07-06 |
EP1550736A4 EP1550736A4 (en) | 2005-07-06 |
Family
ID=19188629
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP02790874A Withdrawn EP1550736A4 (en) | 2001-12-25 | 2002-12-25 | Carburized and quenched member and method for production thereof |
Country Status (6)
Country | Link |
---|---|
US (1) | US20050173026A1 (en) |
EP (1) | EP1550736A4 (en) |
JP (1) | JP4354277B2 (en) |
KR (1) | KR20040088016A (en) |
CN (1) | CN1539026A (en) |
WO (1) | WO2003056054A1 (en) |
Cited By (5)
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EP2138591A1 (en) * | 2008-06-09 | 2009-12-30 | Marco Masnari | Use of a treatment process on coffee mills and coffee mill thus treated |
KR101185060B1 (en) | 2012-03-13 | 2012-09-21 | 동우에이치에스티 주식회사 | Ann's gear automatic transmission with heat treatment |
EP2284287A4 (en) * | 2008-10-08 | 2015-05-20 | Aisin Aw Co | Process for production of carburized part and steel part |
US9617632B2 (en) | 2012-01-20 | 2017-04-11 | Swagelok Company | Concurrent flow of activating gas in low temperature carburization |
US10156006B2 (en) | 2009-08-07 | 2018-12-18 | Swagelok Company | Low temperature carburization under soft vacuum |
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Publication number | Priority date | Publication date | Assignee | Title |
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WO2004059029A1 (en) * | 2002-12-25 | 2004-07-15 | Aisin Aw Co., Ltd. | Carburized and quenched member and method for manufacture thereof |
DE102005061946B4 (en) * | 2004-12-27 | 2013-03-21 | Nippon Steel Corp. | Case hardened steel having excellent tooth surface fatigue strength, gear using the same, and methods of making same |
EP1876256B1 (en) * | 2005-04-28 | 2012-01-18 | Aisin AW Co., Ltd. | Carburized induction-hardened component |
JP4876668B2 (en) * | 2006-03-29 | 2012-02-15 | アイシン精機株式会社 | Heat treatment method for steel members |
US7550048B2 (en) * | 2006-12-15 | 2009-06-23 | Tenneco Automotive Operating Company Inc. | Method of manufacture using heat forming |
DE102010048209C5 (en) | 2010-10-15 | 2016-05-25 | Benteler Automobiltechnik Gmbh | Method for producing a hot-formed press-hardened metal component |
CN102803539B (en) * | 2010-12-08 | 2014-12-03 | 新日铁住金株式会社 | Gas-carburized steel component with excellent surface fatigue strength, gas-carburizing steel material, and process for producing gas-carburized steel component |
US9389155B1 (en) * | 2013-03-12 | 2016-07-12 | United Technologies Corporation | Fatigue test specimen |
CN104384887A (en) * | 2014-09-19 | 2015-03-04 | 马鞍山邦斯科自动化科技有限公司 | Reamer manufacturing method for prolonging service life of reamer |
JP6191630B2 (en) * | 2015-01-15 | 2017-09-06 | トヨタ自動車株式会社 | Workpiece manufacturing method |
CN105525252B (en) * | 2015-12-22 | 2017-12-22 | 中车戚墅堰机车车辆工艺研究所有限公司 | The distortion correcting method and its special tooling of one discharge plate class carburizing and quenching gear |
KR20180099877A (en) | 2016-03-08 | 2018-09-05 | 아이신에이더블류 가부시키가이샤 | Steel parts, gear parts and manufacturing method of steel parts |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH02240249A (en) * | 1989-03-14 | 1990-09-25 | Kobe Steel Ltd | Production of carburized parts reduced in heat treatment strain |
JPH09256102A (en) * | 1996-03-21 | 1997-09-30 | Sumitomo Metal Ind Ltd | Carburized parts excellent in bending strength and impact characteristic |
JPH09287644A (en) * | 1996-04-23 | 1997-11-04 | Toa Steel Co Ltd | High strength low heat treatment deformation gear and manufacture thereof |
US5853502A (en) * | 1995-08-11 | 1998-12-29 | Sumitomo Metal Industries, Ltd. | Carburizing steel and steel products manufactured making use of the carburizing steel |
JP2000273574A (en) * | 1999-03-25 | 2000-10-03 | Mitsubishi Seiko Muroran Tokushuko Kk | Steel for carburizing or carbonitriding treatment |
Family Cites Families (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3006034B2 (en) * | 1990-05-30 | 2000-02-07 | 日産自動車株式会社 | High strength mechanical structural members with excellent surface pressure strength |
JPH0625736A (en) * | 1992-07-10 | 1994-02-01 | Nissan Motor Co Ltd | Manufacture of long life carburized bearing |
JP3894635B2 (en) * | 1997-08-11 | 2007-03-22 | 株式会社小松製作所 | Carburized member, manufacturing method thereof, and carburizing system |
JPH11310824A (en) * | 1998-04-30 | 1999-11-09 | Aisin Aw Co Ltd | Carburized and quenched steel member and its manufacture |
-
2002
- 2002-12-25 EP EP02790874A patent/EP1550736A4/en not_active Withdrawn
- 2002-12-25 JP JP2003556568A patent/JP4354277B2/en not_active Expired - Fee Related
- 2002-12-25 CN CNA028088751A patent/CN1539026A/en active Pending
- 2002-12-25 KR KR10-2004-7002801A patent/KR20040088016A/en not_active Application Discontinuation
- 2002-12-25 US US10/473,716 patent/US20050173026A1/en not_active Abandoned
- 2002-12-25 WO PCT/JP2002/013561 patent/WO2003056054A1/en not_active Application Discontinuation
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH02240249A (en) * | 1989-03-14 | 1990-09-25 | Kobe Steel Ltd | Production of carburized parts reduced in heat treatment strain |
US5853502A (en) * | 1995-08-11 | 1998-12-29 | Sumitomo Metal Industries, Ltd. | Carburizing steel and steel products manufactured making use of the carburizing steel |
JPH09256102A (en) * | 1996-03-21 | 1997-09-30 | Sumitomo Metal Ind Ltd | Carburized parts excellent in bending strength and impact characteristic |
JPH09287644A (en) * | 1996-04-23 | 1997-11-04 | Toa Steel Co Ltd | High strength low heat treatment deformation gear and manufacture thereof |
JP2000273574A (en) * | 1999-03-25 | 2000-10-03 | Mitsubishi Seiko Muroran Tokushuko Kk | Steel for carburizing or carbonitriding treatment |
Non-Patent Citations (6)
Title |
---|
LAMPMAN S.R., ZORC T.B.: "ASM HANDBOOK VOL. 4" August 2001 (2001-08), ASM INTERNATIONAL , UNITED STATES OF AMERICA , XP002309648 * page 348 * * |
PATENT ABSTRACTS OF JAPAN vol. 014, no. 559 (C-0787), 12 December 1990 (1990-12-12) -& JP 02 240249 A (KOBE STEEL LTD), 25 September 1990 (1990-09-25) * |
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 01, 30 January 1998 (1998-01-30) -& JP 09 256102 A (SUMITOMO METAL IND LTD), 30 September 1997 (1997-09-30) * |
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 03, 27 February 1998 (1998-02-27) -& JP 09 287644 A (TOA STEEL CO LTD), 4 November 1997 (1997-11-04) * |
PATENT ABSTRACTS OF JAPAN vol. 2000, no. 13, 5 February 2001 (2001-02-05) & JP 2000 273574 A (MITSUBISHI SEIKO MURORAN TOKUSHUKO KK), 3 October 2000 (2000-10-03) * |
See also references of WO03056054A1 * |
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2138591A1 (en) * | 2008-06-09 | 2009-12-30 | Marco Masnari | Use of a treatment process on coffee mills and coffee mill thus treated |
EP2284287A4 (en) * | 2008-10-08 | 2015-05-20 | Aisin Aw Co | Process for production of carburized part and steel part |
US10156006B2 (en) | 2009-08-07 | 2018-12-18 | Swagelok Company | Low temperature carburization under soft vacuum |
US10934611B2 (en) | 2009-08-07 | 2021-03-02 | Swagelok Company | Low temperature carburization under soft vacuum |
US9617632B2 (en) | 2012-01-20 | 2017-04-11 | Swagelok Company | Concurrent flow of activating gas in low temperature carburization |
US10246766B2 (en) | 2012-01-20 | 2019-04-02 | Swagelok Company | Concurrent flow of activating gas in low temperature carburization |
US11035032B2 (en) | 2012-01-20 | 2021-06-15 | Swagelok Company | Concurrent flow of activating gas in low temperature carburization |
KR101185060B1 (en) | 2012-03-13 | 2012-09-21 | 동우에이치에스티 주식회사 | Ann's gear automatic transmission with heat treatment |
Also Published As
Publication number | Publication date |
---|---|
JPWO2003056054A1 (en) | 2005-05-12 |
WO2003056054A1 (en) | 2003-07-10 |
US20050173026A1 (en) | 2005-08-11 |
EP1550736A4 (en) | 2005-07-06 |
CN1539026A (en) | 2004-10-20 |
JP4354277B2 (en) | 2009-10-28 |
KR20040088016A (en) | 2004-10-15 |
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