US20060130935A1 - Carburized component and method of manufacturing the same - Google Patents

Carburized component and method of manufacturing the same Download PDF

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Publication number
US20060130935A1
US20060130935A1 US11/296,566 US29656605A US2006130935A1 US 20060130935 A1 US20060130935 A1 US 20060130935A1 US 29656605 A US29656605 A US 29656605A US 2006130935 A1 US2006130935 A1 US 2006130935A1
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Prior art keywords
carbide
carburization
steel
depth
comparative
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Abandoned
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US11/296,566
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Atsushi Hattori
Takashi Kano
Tomoko Serikawa
Koki Mizuno
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Honda Motor Co Ltd
Daido Steel Co Ltd
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Honda Motor Co Ltd
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Assigned to DAIDO STEEL CO., LTD., HONDA MOTOR CO., LTD. reassignment DAIDO STEEL CO., LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: MIZUNO, KOKI, SERIKAWA, TOMOKO, HATTORI, ATSUSHI, KANO, TAKASHI
Publication of US20060130935A1 publication Critical patent/US20060130935A1/en
Abandoned legal-status Critical Current

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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
    • 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

Definitions

  • This invention relates to a carburized component and a method of manufacturing the same.
  • Gears used as power transmission components for automobiles and so forth are components suffering from dedendum fractures which occur at the dedendum where bending stress happens, and from slip-induced fracture (pitting) which occurs in the vicinity of the pitch point.
  • a technique of carburizing the surface of the component has, therefore, widely been used for the purpose of fulfilling characteristics enough for withstanding harsh conditions, and further improvement has been made by combining various materials and heat treatments.
  • Patent Document Japanese Laid-Open Patent Publication “Tokkaihei” No. 6-158266
  • the gear has, however, has been demanded to have a larger hardness with the recent increases in the output of automobiles and so forth, but the present situation is that the above-described material is insufficient for fulfilling the requirements.
  • This invention was conceived after considering the above-described situation, and an object thereof is to provide a carburized component realizing higher strength for power transmission components such as gears, and a method of fabricating said components.
  • a carburized component consisting essentially of, in percentages by mass and both ends inclusive, C: 0.1-0.30%, Si: 0.80-1.50%, Mn: 0.30-1.20%, Cr: 2.0-5.5%, and the balance between Fe and inevitable impurities;
  • This invention has basic features as described below. That is, a large amount of fine carbide grains are allowed to precipitate in the surficial portion of the component by high-concentration vacuum carburization, and to substantially exclude the surficial grain boundary oxide layer, to thereby raise the surface hardness and strength.
  • the temper softening resistance in the temperature range from about 200 to 300° C. is enhanced by introducing a large amount of Si, which is realized by the vacuum carburization, and thereby a desirable level of surface fatigue strength can be obtained.
  • C is an essential element for ensuring a necessary level of strength for the component, and is necessary to contain an amount of 0.10% or more.
  • an excessively large content thereof increases the hardness of the material, thus degrading the machinability, and thereby making the machining of the component difficult.
  • the upper limit is therefore adjusted to 0.30%.
  • Si is an element to be contained as a deoxidizing element acting in the process of melting and plays an important role in this invention.
  • the element dissolves into the solid matrix to thereby raise the temper softening resistance, so that a high level of surface fatigue strength can be obtained.
  • the element can also suppress growth of coarse carbide grains, because it shows only a small solid solubility into the carbide and raises the Si concentration in the base metal.
  • Si showing only a small solid solubility into the carbide concentrates in the matrix, and further improves the temper softening resistance of the matrix.
  • the element is necessarily contained to an amount of 0.80% or more in order to obtain this effect.
  • an excessive content of the element inhibits precipitation and the carburization surface reaction of the carbide which thereby distinctively degrades the carburization property, and also degrades the ductility, which thereby makes cracking more likely to occur in the process of plastic working.
  • the upper limit of the content is therefore limited to 1.50%.
  • Si is an element promoting oxidation of the grain boundary in the process of general gas carburization, and the grain boundary oxidation layer is causative of lowering the impact strength and fatigue strength of dedendum.
  • the gas carburization therefore cannot add a large amount of Si, whereas the vacuum carburization as described in the above can clear the problem of grain boundary oxidation, and make it possible to obtain a high-Si-content component.
  • Mn is an element to be contained as a deoxidizing element acting in the process of melting, and has an effect of improving the hardening property, so that it is necessary to contain an amount of 0.30% or more.
  • elements having an effect of improving the hardening property, such as Cr are to be concomitantly contained, wherein the elements such as Cr, capable of forming the carbide, may sometimes result in only an insufficient hardening property even under a raised Cr content or the like, depending on carbide content. It is therefore effective to adjust the Mn content in order to obtain a necessary level of hardening property.
  • an excessive content degrades the machinability due to an increase in the hardness of the material, thus the upper limit is adjusted to 1.20%.
  • Cr is an element playing an important role in this invention. This is necessary to contain an amount of 2.0% or more, as a carbide-forming element and as an element improving the hardening property. On the other hand, an excessive content of the element degrades the machinability due to increased hardness of the material, and makes a network-structured carbide more likely to be generated in the grain boundary. The upper limit of the content is therefore limited to 5.5%.
  • Mo binds with C, similarly to Cr, to produce the carbide, and has an effect of improving the pitting strength by raising the softening resistance over the temperature range from 200° C. to 300° C.
  • the element is preferably contained to an amount of 0.2% or more, for the purpose of obtaining these effects.
  • an excessive content of the element degrades the machinability due to an increase in hardness of the material, and increases the material cost.
  • the upper limit of the content is, therefore, preferably limited to 1.0%.
  • V binds with C, similarly to Cr and Mo, to produce the carbide, and has an effect of improving the pitting strength by raising the softening resistance, through production of an MC-type carbide.
  • the element is preferably contained to an amount of 0.2% or more, for the purpose of obtaining these effects.
  • an excessive content of the element degrades the machinability due to an increase in hardness of the material.
  • the upper limit of the content is, therefore, preferably limited to 1.0%.
  • Vacuum Carburization (at 1,000 Pa or Below)
  • the carburized component of this invention is subjected to vacuum carburization.
  • the vacuum carburization makes it possible to decrease the growth of the grain boundary oxide layer, and is therefore successful in raising the strength of the carburized component.
  • Si is added as an essential ingredient.
  • Si is an element promoting the grain boundary oxidation in the process of the general gas carburization, and such grain boundary oxidation is causative of reducing the impact strength and fatigue strength of the dedendum. It is, therefore, extremely difficult for the general gas carburization to achieve a large Si content.
  • the vacuum carburization can, however, suppress formation of the grain boundary oxide layer, and can readily realize a high Si content.
  • the grain boundary oxide layer causes lowering in the fatigue strength and anti-pitting strength, wherein the degree of the lowering becomes larger as the depth increases.
  • the depth of grain boundary layer from the surface of the steel after the vacuum carburization is adjusted to 1 ⁇ m or less.
  • the general carburization is normally carried out as an eutectic carburization of the surface of steel, targeted at an eutectic C content of 0.8%.
  • this invention is aimed at improving the anti-pitting property through precipitation of the carbide in the surficial layer of the steel to thereby enhance the softening resistance, so that it is necessary to contain C to an amount of the eutectic C content (0.8%) or more.
  • the surface fatigue strength cannot be improved even if the carbide is allowed to precipitate, unless the carbide is obtained with a content necessary for improving the softening resistance, so that it is also necessary to make C contained to an amount sufficient enough for the improvement.
  • the mean C concentration over the range from the surface of steel to a depth of 0.2 mm (also referred to as surface C concentration, hereinafter) is adjusted to 1.2% or more.
  • the reason why the range is defined from the surface of the steel to a depth of 0.2 mm is that the hardness in such range is important from the viewpoint of the pitting resistance.
  • an excessive content results in production of large carbide grains, and causes insufficient hardening property of the base material, thereby degrading the strength.
  • the upper limit of the surface C concentration is therefore limited to 3.0%.
  • Ratio of Carbide Area Over the Range from the Surface to a Depth of 50 ⁇ m 15% or More and 60% or Less
  • Precipitation of the carbide raises the surface hardness, improves the softening resistance over the temperature range from 200° C. to 300° C., and improves the anti-pitting resistance.
  • a ratio of carbide area over the range from the surface to a depth of 50 ⁇ m of less than 15% cannot fully improve the softening resistance, and cannot obtain a sufficient effect of improving the strength.
  • the ratio of carbide area exceeding 60% can improve the softening resistance, but lowers the surface fatigue and bending fatigue strength, because the carbide of a larger grain size is more likely to precipitate along the grain boundary in a network manner.
  • An exemplary observation of the obtained carbide is shown in FIG. 4 .
  • the carbide is a hard grain, and may serve as a starting point of fatigue fracture, similarly to non-metallic inclusions such as Al oxide and Ti nitride.
  • a smaller carbide is therefore more preferable, wherein the grain size of which is necessarily controlled to as small as 10 ⁇ m or below, so as not to allow the carbide to exist as the starting point of fatigue fracture. It is therefore controlled so that the carbide precipitates in a finely dispersed manner, so that the carbide having a grain size of 10 ⁇ m or less accounts for 90% or more of the entire portion.
  • An exemplary observation of the obtained carbide is shown in FIG. 4 .
  • a method of manufacturing a carburized component of this invention subjects the steel containing the above-described steel ingredients to a primary carburization at a temperature of Acm or above, then rapidly cools the steel to as low as point A1 or below, and then subjects the steel to a secondary carburization at a temperature of point A1 or above and Acm or below. More specifically, as shown in FIGS. 1A and 1B , the primary carburization is carried out so as not to precipitate the carbide, at a temperature of as high as Acm or above, allowing a large solid solubility limit of C and allowing no carbide to precipitate (between points “a” and “b”).
  • the steel is rapidly cooled so as to dissolve C into a solid super-saturated manner (between points “b” and “c”). Thereafter, the steel is again heated to as high as point A1 or above, to thereby allow fine carbide nuclei to uniformly precipitate from the base material super-saturated with C (between points “d” and “e”, see the upper drawing in FIG. 2 ), and the steel is further subjected to a secondary carburization so as to grow the nuclei (between points “e” and “f”, see the lower drawing in FIG. 2 ).
  • Such multi-stage carburization can realize a high-C-concentration carburization with a controlled fine dispersion of the carbide, without allowing the network-structured carbide to precipitate.
  • the carburization carried out to as far as the high-C-concentration region before point Acm makes the network-structured coarse carbide very likely to produce.
  • the carburization therein is carried out by vacuum carburization (at 1,000 Pa or below) as described in the above.
  • Shot peening S/P
  • water jet peening W/J
  • FIGS. 1A and 1B are drawings explaining carburization involved in the method of manufacturing a carburized component of this invention
  • FIG. 2 shows a schematic sectional view and a drawing of an observed section of steel during the carburization shown in FIG. 1 ;
  • FIG. 3 shows a drawing explaining an exemplary carburization different from this invention, and a drawing of an observed section
  • FIG. 4 is a drawing of an observed section of the carburized component of this invention.
  • each of the steels having chemical compositions listed in Table 1 was melted in a 150-kg high-frequency vacuum induction furnace.
  • the obtained steel ingot was rolled or hot forged so as to produce a 90-mm-diameter round rod, or further hot-forged, if necessary, so as to obtain steel bar shape having a diameter of 22 to 32 mm, which was used as a test piece.
  • test pieces were subjected to the following evaluations.
  • the manufacturability was evaluated by measuring the hardness after annealing.
  • a round test piece rod of 32 mm in diameter and 100 mm in length was subjected to annealing at 920° C. for 1 hour, further annealed at 760° C. for 5 hours, and the hardness at the position of R/2 on the transverse section was measured.
  • the measurement of hardness conforms to JIS Z 2245 (B-scale), with a target value of HRB90 or smaller
  • a round test piece rod 10 mm in diameter and 100 mm in length was fabricated, as a test piece for carburization property, from a forged steel bar 22 mm in diameter.
  • the carburization was carried out in a vacuum carburization furnace, using propane as the carburization gas, wherein the surface C concentration was controlled by adjusting flow rate of propane gas, diffusion time, and carburization temperature.
  • the carburization was carried out at two levels of conditions so as to achieve a surface C concentration of 1.5% and 2.5%, respectively.
  • Example 3 the carburization was carried over the surface range of C concentration from 0.8 to 3.2%, in order to investigate influences of the surface C concentration.
  • the carburization conditions are as follows.
  • test piece was carburized at 1,100° C. for 70 minutes so as to adjust the C concentration to the topmost surface to about 1.2%, and then rapidly cooled by cooling gas to a temperature range as low as 500° C. or below, to thereby allow C to intrude into the steel to at a high concentration range so as not to be causative of precipitation of the carbide.
  • the test piece was subjected to the precipitation treatment by keeping it in the temperature range from 850° C. to 900° C., depending on the target carburization concentration, further carburized in the temperature range from 850° C. to 1,000° C. for 60 to 90 minutes depending on the target C concentration, and was hardened by immersing it into an oil bath kept at 130° C. After the hardening, the test place was annealed at 180° C. for 120 minutes.
  • Results of the evaluation are listed in Table 2.
  • Results of Example 3 obtained by varying the surface C concentration are listed in Table 3.
  • C concentration was measured using a grinding chip obtained from the surface to a depth of 0.2 mm of the treated test piece.
  • the transverse section of the carburized and annealed test piece rod was polished, corroded with picral, to a portion of a depth of 50 ⁇ m from the topmost surface was photographed under a SEM (at a 3,000 ⁇ magnification of observation), and the ratio of area was measured by image analysis.
  • the test piece was observed under the same conditions as described in the above, and the area ratio occupied by the carbide grain sized 10 ⁇ m or less was measured.
  • test piece was observed under the same conditions as those described in the above, and presence or absence of the network-structured carbide was investigated.
  • the transverse section of the carburized, annealed test piece rod was polished, corroded with nital, to a portion of a depth of 50 ⁇ m from the topmost surface was photographed under an optical microscope, and presence or absence of the incompletely-hardened structure was investigated.
  • the transverse section of the carburized and annealed rod test piece was polished, the resultant surface in an uncorroded state was observed under an optical microscope, and the depth of the layer appearing as black along the grain boundary at the topmost surface was measured.
  • the carburized and annealed test piece rod was further annealed at 300° C. for 180 minutes, the transverse section was polished, and the hardness at a depth of 50 ⁇ m from the topmost surface was measured.
  • the hardness herein conforms to JIS Z 2244 (Hv0.3), wherein a value of Hv750 or above is considered as an index ensuring a sufficient effect of improving the strength ( ⁇ 30%: in comparison with SCR420 gas eutectic carburized steel).
  • Hv0.3 JIS Z 2244
  • Hv750 or above is considered as an index ensuring a sufficient effect of improving the strength ( ⁇ 30%: in comparison with SCR420 gas eutectic carburized steel).
  • Comparative Example 4 too large in the Si content, raises a problem in the manufacturability, inhibits the carburization property, and cannot allow the carburization to proceed to a sufficient degree.
  • Comparative Examples 5 and 7 low in the Cr and Mn contents, which give only poor levels of hardening property, show the incompletely-hardened structure, and may undesirably degrade the strength.
  • the carburization targeted at a surface C concentration of less than 1.2% is successful in improving the surface fatigue strength, but unsuccessful in obtaining a sufficient effect for improving the strength ( ⁇ 30%).
  • the carburization targeted at a surface concentration exceeding 3.0% is successful in obtaining a sufficient level of 300° C. temper hardness, but shows the network-structured carbide and coarse carbide, and is unsuccessful in obtaining a sufficient effect for improving the strength.
  • the surface fatigue strength was evaluated using a roller pitting tester, wherein the surface fatigue strength was defined as the pressure on the load surface not causative of pitting over 107 cycles of the test. More specifically, a 32-mm-diameter round rod was softened by keeping it heated at 950° C., followed by gradual cooling, and was then machined to fabricate a roller pitting test piece having a diameter of test portion of 26 mm. A roller correspondent to the test piece was configured using SUJ2, and subjected to quench-and-temper so as to attain a hardness of HRC61. The radii of curvature of large rollers are 150R and 700R.
  • the carburization was simultaneously carried out with the carburization carried out for basic evaluation of the inventive steel.
  • a portion of the roller pitting test piece after the carburization was tempered at 300° C. for 3 hours, and evaluation was also made on the carbon concentration, ratio of the carbide area, the maximum carbide size and temper hardness.
  • the surface fatigue strength of each material was expressed by an index, assuming the surface fatigue strength of gas-eutectic-carburized JIS-SCR420 material is 1.0.
  • a sufficient effect of improving the strength by 30% or more as compared with gas-eutectic-carburized JIS-SCR420H steel was targeted.
  • Example 1 805 1.44
  • Example 2 798 1.40
  • Example 3 816 1.45
  • Example 4 825 1.51
  • Example 5 800 1.49
  • Example 6 804 1.46
  • Example 7 813 1.43
  • Example 8 841 1.54
  • Example 9 832 1.52
  • Comparative Example 1 shows only a low strength due to poor strength of the core portion. Comparative Examples 2, 4, 6, 9 and 10 are successful in sufficiently improving the strength, but raise a problem in the manufacturability. Comparative Examples 3 and 8 show growth of the network-structured carbide and other coarse carbide, and fail in obtaining sufficient levels of effect for improving the strength. Comparative Examples 5 and 7, having low contents of Cr and Mn, show only poor hardening properties as indicated by the incompletely-hardened structure, and fail in obtaining sufficient levels of effect for improving the strength.
  • the carburized component of this invention was confirmed as having a large amount of fine carbide grains precipitated in the surficial portion thereof, as being substantially free from the grain boundary oxide layer in the surficial portion, and being excellent in the areas of surface hardness and strength.
  • FIG. 1A A first figure.
  • FIG. 1B FIG. 3

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JP2004358617A JP4188307B2 (ja) 2004-12-10 2004-12-10 浸炭部品及びその製造方法

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US20070246126A1 (en) * 2006-04-20 2007-10-25 Daido Steel Co., Ltd. Carburized component and manufacturing method thereof
WO2008124239A1 (en) * 2007-04-06 2008-10-16 Swagelok Company Hybrid carburization with intermediate rapid quench
EP2085493A4 (en) * 2006-11-06 2009-11-25 Honda Motor Co Ltd PROCESS FOR MANUFACTURING HIGH CONCENTRATION CEMENTYED STEEL
US20100037991A1 (en) * 2007-04-05 2010-02-18 Swagelok Company Diffusion promoters for low temperature case hardening
US20100159235A1 (en) * 2008-12-18 2010-06-24 Scott Alan Johnston Wear component with a carburized case
WO2010071014A1 (en) * 2008-12-19 2010-06-24 Yamaha Hatsudoki Kabushiki Kaisha Connecting rod, internal combustion engine, transportation apparatus, and method of producing connecting rod
US20110030849A1 (en) * 2009-08-07 2011-02-10 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
US11326220B2 (en) 2018-06-18 2022-05-10 Komatsu Ltd. Method for producing machine component

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JP2010007117A (ja) * 2008-06-25 2010-01-14 Sanyo Special Steel Co Ltd 高強度浸炭部品の製造方法
JP2011179026A (ja) * 2010-02-26 2011-09-15 Sanyo Special Steel Co Ltd 耐繰返し衝撃特性に優れた大形歯車用鋼
WO2012032630A1 (ja) 2010-09-09 2012-03-15 トヨタ自動車株式会社 歯車
JP6432932B2 (ja) * 2014-09-01 2018-12-05 山陽特殊製鋼株式会社 耐ピッチング性および耐摩耗性に優れる高強度高靱性機械構造用鋼製部品およびその製造方法
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US7967921B2 (en) 2006-04-20 2011-06-28 Daido Steel Co., Ltd. Carburized component and manufacturing method thereof
US20070246126A1 (en) * 2006-04-20 2007-10-25 Daido Steel Co., Ltd. Carburized component and manufacturing method thereof
EP2085493A4 (en) * 2006-11-06 2009-11-25 Honda Motor Co Ltd PROCESS FOR MANUFACTURING HIGH CONCENTRATION CEMENTYED STEEL
US20100126632A1 (en) * 2006-11-06 2010-05-27 Honda Motor Co., Ltd. Manufacturing method for high-concentration carburized steel
US20100037991A1 (en) * 2007-04-05 2010-02-18 Swagelok Company Diffusion promoters for low temperature case hardening
WO2008124239A1 (en) * 2007-04-06 2008-10-16 Swagelok Company Hybrid carburization with intermediate rapid quench
US20100116377A1 (en) * 2007-04-06 2010-05-13 Swagelok Company Hybrid carburization with intermediate rapid quench
US20100159235A1 (en) * 2008-12-18 2010-06-24 Scott Alan Johnston Wear component with a carburized case
WO2010071014A1 (en) * 2008-12-19 2010-06-24 Yamaha Hatsudoki Kabushiki Kaisha Connecting rod, internal combustion engine, transportation apparatus, and method of producing connecting rod
US20110030849A1 (en) * 2009-08-07 2011-02-10 Swagelok Company Low temperature carburization under soft vacuum
US9212416B2 (en) 2009-08-07 2015-12-15 Swagelok Company Low temperature carburization under soft vacuum
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
US11326220B2 (en) 2018-06-18 2022-05-10 Komatsu Ltd. Method for producing machine component

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