[go: up one dir, main page]

WO2018061197A1 - Produit forgé thermiquement traité en acier de cémentation - Google Patents

Produit forgé thermiquement traité en acier de cémentation Download PDF

Info

Publication number
WO2018061197A1
WO2018061197A1 PCT/JP2016/079101 JP2016079101W WO2018061197A1 WO 2018061197 A1 WO2018061197 A1 WO 2018061197A1 JP 2016079101 W JP2016079101 W JP 2016079101W WO 2018061197 A1 WO2018061197 A1 WO 2018061197A1
Authority
WO
WIPO (PCT)
Prior art keywords
steel
temperature
carburizing
forging
treated product
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2016/079101
Other languages
English (en)
Japanese (ja)
Inventor
芳彦 鎌田
康裕 中西
智晃 端野
利信 宮田
建壮 高橋
絢子 服崎
隆司 兵恵
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Changzhou Gohsyu Automobile Parts Co Ltd
Gohsyu Corp
Original Assignee
Changzhou Gohsyu Automobile Parts Co Ltd
Gohsyu Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Changzhou Gohsyu Automobile Parts Co Ltd, Gohsyu Corp filed Critical Changzhou Gohsyu Automobile Parts Co Ltd
Priority to PCT/JP2016/079101 priority Critical patent/WO2018061197A1/fr
Priority to PCT/JP2017/025016 priority patent/WO2018061396A1/fr
Publication of WO2018061197A1 publication Critical patent/WO2018061197A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • the present invention relates to a forged heat-treated product using bare-fired steel as a raw material.
  • CVT Continuous Variable Transmission
  • transmission gears transmission gears
  • differential gears transmission gears
  • hot forging is performed using bare-fired steel.
  • machining was performed to form the final part, carburizing and quenching was performed, and finishing was further performed to obtain the final part.
  • the present invention examines various simplifications of the process, and (1) molding by a method combining hot forging and cold working or vacuum carburizing. Even if the heat treatment time is shortened by high-temperature carburization, (2) If the steel for forging, forging heating temperature and normalizing conditions are optimized, the machinability is good and the carburizing treatment can be performed in the practical temperature range.
  • the present inventors have found that a forged heat-treated product of case hardening steel that does not cause coarsening of austenite grains can be provided.
  • the forged heat-treated product of the case-hardened steel of the present invention uses the case-hardened steel as a raw material and is subjected to hot forging and heat treatment in the following steps (1) to (3).
  • Manufactured (1) A step of heating the material at 1100 to 1280 ° C. and forging at a temperature of 950 to 1200 ° C.
  • the temperature is raised in the range of 0.10 to 0.40 ° C./s in the temperature raising process of the normalization, The time from 860 ° C. to reaching 860 ° C.
  • the forged parts can disperse fine precipitates such as AlN (aluminum-nitrogen) precipitates, and abnormal grain growth of austenite grains is suppressed during carburizing, resulting in carburizing.
  • the carburizing and quenching distortion of the parts will be improved.
  • hardened steel means “hardened steel” defined in JIS G 0203.
  • the “temperature increase rate” or “cooling rate” refers to an average temperature increase rate or average cooling rate between 800 ° C. and 500 ° C.
  • the forged heat-treated product of the case-hardened steel of the present invention produced in this way has 20 to 10,000 AlN precipitates with a particle size of 1 to 100 nm per 1 ⁇ m 2 and has a unit area. It is characterized by ferrite + pearlite structure steel finely dispersed and precipitated with a correlation of f ⁇ x when the number of hits is f and the average particle diameter is xnm.
  • the forged heat-treated products of the case-hardened steel of the present invention are carburized parts used for drive system parts of automobiles and construction machinery, among others, mechanical parts used as CVT, mission gear, differential gear, etc.
  • Forged heat-treated products of the case-hardened steel of the present invention utilize trace elements such as Al and N contained in the steel, optimize the heating temperature and forging temperature of hot forging, and the subsequent heat treatment conditions. Precipitates having a particle size of 1 to 100 nm, 20 to 10000 per unit area (1 ⁇ m 2 ), f per unit area, and average particle size xnm, f ⁇ x
  • trace elements such as Al and N contained in the steel
  • AlN precipitate shown here a 10 mm square test piece was collected from the surface layer of the forged heat-treated product, embedded and polished, corroded with 1.5% nital solution for about 30 seconds, and after gold deposition, Fe— Observed with SEM. In the measurement, four fields of view were observed at a magnification of 40,000 times, and the size and number of AlN precipitates were measured from a total test area of 30 ⁇ m 2 . Since the AlN precipitates were mainly strip-shaped, and some of them were agglomerated, the measured area of the AlN precipitates was replaced with a circular area, and the diameter of the circle was taken as the particle diameter.
  • Identification as an AlN precipitate was performed by EDX analysis (Energy dispersive X-ray spectrometry), but it was difficult to discriminate when the size was 100 nm or less. Therefore, a 500 nm level precipitate estimated to be insoluble is identified, and only those having an Al peak are judged as AlN, and those below 100 nm existing in the vicinity thereof are assumed to be AlN precipitates.
  • the particle size and number were measured. In order to calculate the pinning force, it is necessary to measure the number per unit volume. However, the number per unit area is measured for SEM (Scanning Electron Microscope) observation, and the number per 1 ⁇ m 2 is expressed as a notation. It was decided to use.
  • the average particle diameter was obtained by integrating the individual particle diameters and using a simple average value as the average particle diameter.
  • the pinning effect thereof is small compared with the precipitates having a size of 1 to 100 nm, so the precipitates exceeding 100 nm are excluded from the target.
  • size of 100 nm or less was extract
  • FIB Flucused Ion Beam
  • the particle diameter was 1 to 100 nm.
  • the treatment is performed at 930 ° C. for 6 hours and in the austenite region for a long time at a high temperature.
  • coarsening should not occur because it affects the fatigue strength and wear resistance of automobile parts after carburizing and quenching.
  • fine precipitates such as AlN are utilized.
  • Non-Patent Document 4 a large number of such fine precipitates are precipitated in steel, and grain boundaries during carburizing treatment are used. It is known as an effective method to pin the movement (granular growth).
  • the range is set to 1 to 100 nm.
  • the number per unit area (1 ⁇ m 2 ) was 20 or more and 10,000 or less. In the case of 20 or less per unit area, there is no sufficient pinning effect, and in order to deposit 10000 or more, it is necessary to make AlN solid solution once at the forging heating temperature and reprecipitate. Since there are also restrictions on the forging heating temperature, there is an upper limit for the amount of Al and N added, while the amount of precipitation depends on the amount of solid solution, so the upper and lower limits are naturally determined.
  • the number per unit area (1 ⁇ m 2 ) is set to 20 or more and 10,000 or less from a practical aspect.
  • the number f of fine precipitates per unit area and the average particle diameter x were controlled by the correlation of f ⁇ x.
  • f is the number of fine precipitates such as AlN per unit area (1 ⁇ m 2 )
  • x is the average particle diameter of the fine precipitates
  • the particle diameter range is defined as 1 to 100 nm.
  • the particle size was also defined as 1 to 100 nm.
  • the number of fine precipitates per unit area and the average particle size cannot be controlled independently, but can be controlled within a certain addition amount.
  • the finer the pinning effect the greater the pinning effect, and the greater the pinning effect, the smaller the effect. That is, as the size of the precipitates approaches 100 nm, the pinning effect per piece becomes smaller, so it is necessary to increase the number per unit area to ensure the grain growth inhibiting force due to a certain pinning effect. Therefore, the average particle diameter (x) and the number per unit area (f) are controlled by the correlation of f ⁇ x.
  • case hardening steel is defined as low carbon steel and low carbon alloy steel, and is mainly defined as the name of steel used for carburized parts. ing.
  • Nb 0.015 to 0.060% by weight
  • Nb is an element required to produce Nb carbide and Nb carbonitride by combining with carbon C and nitrogen N in steel, and has an effect of preventing austenite grains from coarsening during carburization. . If it is less than 0.015% by weight, the effect of preventing grain coarsening is poor.
  • Ti is an element required to form Ti carbide and Ti carbonitride, or NbTi carbide and NbTi carbonitride by combining with carbon C and nitrogen N in steel, as with Nb. This has the effect of preventing coarsening of the austenite grains. If it is less than 0.015% by weight, the effect of preventing grain coarsening is poor.
  • the upper limit value was specified to 0.050% by weight.
  • Hot forging heat treatment The manufacturing process of CVT, mission gear, differential gear, etc., produced using hardened steel is (1) hot forging, (2) normalizing heat treatment, (3) shot peening, (4) It consists of a plurality of processes such as machining, (5) carburizing treatment, and (6) finishing.
  • the present invention is intended for CVT, mission gear, differential gear, and the like, and among the steps (1) to (6), the steps (1) and (2)
  • a hot forging heat-treated product composed of FIG. 1 briefly shows the outline. The restrictions of the manufacturing conditions defined for each process will be described below.
  • Hot forging for example, the material steel is forged by heating from room temperature to a predetermined temperature by high-frequency heating, but the temperature rise time is 10 to 120 seconds. Is common. Since it varies depending on the capacity of the apparatus and the size of the material, only a guide is described here.
  • C Forging temperature (950-1200 ° C) Hot forging is often performed for the purpose of forming a metal hot and adjusting the size of the metal structure (sizing). In order to make the metal structure sized, it is generally performed by utilizing recrystallization by hot working, and is preferably performed at 950 ° C. or higher. In addition, when hot forging is performed at a temperature of 950 ° C.
  • the structure after hot forging of the hardened steel is generally a mixed structure of ferrite + pearlite + partially bainite.
  • Automotive parts such as CVT, transmission gear, and differential gear manufactured using the hot forging process are formed by machining after hot forging, and are subjected to surface hardening treatment such as carburizing and quenching. Used as a part.
  • a hard metal structure such as a bainite structure is often mixed in the hot forging state, which degrades the machinability (increased tool wear and reduced chip cutting performance).
  • Non-Patent Document 1 if there is a difference in the metal structure before carburizing treatment, the austenite initial grains are greatly affected, and if the initial grains are small, the driving force for grain growth of austenite grains increases. In order to suppress the growth, it is important to reduce the grain growth driving force by increasing the ferrite + pearlite structure before carburizing and increasing the austenite initial grains during carburizing treatment.
  • the quenched structure after carburizing takes over the mixed grains of the previous structure, it is said that the fatigue strength reduction and wear of the carburized and quenched parts are promoted and carburizing and quenching distortion occurs, and the cooling rate after forging is the metal structure.
  • the cooling rate after hot forging was set to natural cooling or 0.10 to 2 ° C./s.
  • the normalizing treatment needs to be a ferrite + pearlite structure after cutting, and is generally a normalizing treatment.
  • the temperature raising rate of the normalizing treatment needs to be carried out at a temperature rising rate of 0.10 to 0.40 ° C./s up to a predetermined normalizing temperature. That is, as shown in Non-Patent Document 2, AlN precipitates are likely to precipitate during the temperature raising process of the normalization treatment, and in particular, when AlN precipitation treatment is performed at 600 ° C. to 700 ° C., the austenite coarsening start temperature increases. It is known that it is difficult to coarsen (Non-patent Document 3). In order to finely deposit the AlN precipitate having the effect of preventing the coarsening, precipitation in the temperature rising process is more effective than the temperature lowering process as described in Non-Patent Document 2.
  • the normalization temperature is usually determined within a practical range between the part using side (for example, a car manufacturer) and the part material supplying side (for example, a forging manufacturer), and in the range of 900 to 950 ° C. It is decided each time. In the case of bare steel, 910 ° C or 920 ° C is often used. In this patent, a temperature range of 900 to 950 ° C. is assumed as the normalizing temperature, but the normalizing temperature is not particularly defined. (C) Processing time from 860 ° C.
  • Non-patent Documents 1 and 2 it has been reported that AlN precipitates partially dissolve or agglomerate and coarsen. That is, increasing the treatment time during this period promotes the aggregation and coarsening of AlN precipitates, and reduces the pinning force of austenite grain growth as shown in Non-Patent Document 4. That is, from the viewpoint of suppressing the growth of the austenite grains at the carburizing temperature, it is preferable to shorten the time between them as much as possible.
  • Cooling rate during normalizing treatment The cooling rate from the normalizing temperature to 550 ° C. was 0.10 to 0.30 ° C./s. This means a cooling rate for obtaining a ferrite + pearlite structure.
  • the slower the cooling rate the higher the transformation from high temperature, so that a coarser ferrite + pearlite structure can be obtained.
  • Non-Patent Document 1 it is said that the ferrite + pearlite structure with a coarser metal structure before carburizing has a larger initial austenite grain size during carburizing heat treatment, lowers the driving force for grain growth, and can increase the coarsening start temperature. .
  • the case-hardened steel used here needs to be slower than 0.30 ° C./s in order to obtain a ferrite + pearlite structure.
  • the cooling rate is set to 0.10 to 0.30 ° C./s.
  • Table 1 shows chemical components of test materials (steel materials) used in Examples and Comparative Examples.
  • Steel A to steel C are steel materials included in the component range of this patent, while steel D is a steel material in which the addition amounts of Al and N deviate significantly from the component range of this patent.
  • the raw steel was melted using a vacuum melting furnace, cast into a mold, die cut, and processed into a round bar having a diameter of 80 mm by hot forging. Then, it peeled off to a 70-mm-diameter round bar by peeling, and it used for the trial manufacture for demonstrating the effect of this invention.
  • Table 2 shows specific examples of forging heat treatment prototypes.
  • a steel material with a diameter of 70 mm was used.
  • the metal structure and surface hardness were investigated.
  • the metal structure was measured by measuring the internal structure near 3 mm from the surface part of the part, and the hardness was measured by measuring the surface hardness (HB) and converted to HRB hardness.
  • the metal structure and hardness are used for judgment of machinability.
  • bainite is mixed in the metal structure and becomes harder than HRB87, the chips are connected to hinder the operation of the automatic processing line. Therefore, the ferrite + pearlite structure and HRB ⁇ 87. was used as a criterion.
  • Table 2 specifically shows examples and comparative examples, which will be described below. Examples of the present invention are shown in Prototype Examples 1 to 3 in Table 2, and Comparative Examples are shown in Prototype Examples 4 to 8 in Table 2.
  • the prototype No. Examples 1 to 3 are examples of this patent that satisfy the components of the steel material of this patent and satisfy the forging conditions and heat treatment conditions.
  • the obtained metal structure was a ferrite + pearlite structure, and the machinability was also in the range of 80 to 85 in HRB hardness, which was a satisfactory level.
  • the shot peening process was also 50 to 60%, which was simplified to about half the processing time as compared with the normal shot peening process.
  • the carburizing and quenching particle size was 25 ⁇ m or less, and no coarsening occurred.
  • Prototype No. No. 4 is a component system in which the contents of Al and N deviate significantly from the components of this patent, and NG was selected because coarsening could not be suppressed even when carried out under the production conditions of this patent. This is considered to be because the solid solution of AlN could not be sufficiently achieved even by heating at 1250 ° C.
  • Prototype No. No. 5 has a forging temperature as low as 950 ° C., and it is considered that AlN was processed and precipitated during forging, resulting in a weak pinning effect during carburizing and coarsening.
  • the cooling rate after normalization is as high as 0.90 ° C./s
  • the surface hardness is HRB87
  • the metal structure is ferrite + pearlite + bainite. If the cooling rate during normalization was not slower than 0.30 ° C./s, it was found that bainite was mixed into the metal structure to form a hard structure, and the machinability deteriorated, so that it was determined as NG.
  • Prototype No. No. 6 has a processing time of 860 ° C. or higher at the time of normalization of 3000 seconds, and the prototype is manufactured under conditions that greatly exceed 1800 s. In this way, when the treatment for 1800 s or more is performed in the temperature range of 860 ° C.
  • the AlN precipitates exhibiting the pinning effect are dissolved and agglomerated to lose the pinning effect, and the carburized and quenched ⁇ grains are coarsened.
  • the shot peening time is 300%, and it has been found that time is required for descaling due to an increase in the amount of scale generation, which is NG.
  • Prototype No. No. 7 is a component system in which Nb and Ti, both of the atomizing elements, are added together, and the forging heating temperature is lowered to 1000 ° C., and if the forging temperature is lowered to 940 ° C., even if other production conditions are satisfied, As a result, granulation could not be prevented and it was determined as NG.
  • Prototype No. 8 the heating rate during normalization was increased to 1.00 ° C./s, and the cooling rate during normalization was increased to 0.85 ° C./s.
  • the component of the steel material is a component system in which Al and N are deviated to a high level, and sufficient AlN solid solution cannot be achieved even by 1200 ° C. forging heating, and in addition, it is a prototype condition in which the heating rate and cooling rate during normalization are increased. .
  • the carburized and quenched ⁇ grains are coarse.
  • FIG. 2 shows the correlation between the number (f) of AlN precipitates per unit area (1 ⁇ m 2 ) and the average particle diameter (xnm).
  • the forged heat-treated product of the hardened steel according to the present invention has been described based on the embodiment.
  • the present invention is not limited to the configurations described in the above examples, and does not depart from the spirit of the present invention.
  • the configuration can be changed as appropriate.
  • the forged heat-treated products of the case-hardened steel of the present invention are excellent in machinability by (1) optimizing hot forging and heat treatment, and (2) controlling the precipitation form of fine precipitates in the forged heat-treated products.
  • austenite grain coarsening can be suppressed at the same time, and carburizing and quenching distortion can be reduced, carburized parts used in driving system parts of automobiles and construction machinery, among others, CVT, mission gear, differential gear, etc. It can use suitably for the use which manufactures the machine parts used.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
  • Forging (AREA)

Abstract

Afin de fournir un produit forgé thermiquement traité en acier de cémentation qui présente une bonne usinabilité et qui ne cause pas de grossissement de grain d'austénite pendant un traitement de cémentation dans une plage de température pratique, un produit forgé thermiquement traité en acier de cémentation selon la présente invention comprend un acier à structure de ferrite-perlite qui a 20 à 10 000 particules par µm2 d'un précipité d'AlN ayant une taille de particule de 1 à 100 nm et qui est le résultat d'une précipitation de dispersion fine correspondant à la corrélation f ≥ x, le nombre de particules par unité de surface étant désigné par f et la taille moyenne de particule étant désignée par x (nm).
PCT/JP2016/079101 2016-09-30 2016-09-30 Produit forgé thermiquement traité en acier de cémentation Ceased WO2018061197A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
PCT/JP2016/079101 WO2018061197A1 (fr) 2016-09-30 2016-09-30 Produit forgé thermiquement traité en acier de cémentation
PCT/JP2017/025016 WO2018061396A1 (fr) 2016-09-30 2017-07-07 Produit forgé, traité thermiquement en acier de cémentation

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/JP2016/079101 WO2018061197A1 (fr) 2016-09-30 2016-09-30 Produit forgé thermiquement traité en acier de cémentation

Publications (1)

Publication Number Publication Date
WO2018061197A1 true WO2018061197A1 (fr) 2018-04-05

Family

ID=61759349

Family Applications (2)

Application Number Title Priority Date Filing Date
PCT/JP2016/079101 Ceased WO2018061197A1 (fr) 2016-09-30 2016-09-30 Produit forgé thermiquement traité en acier de cémentation
PCT/JP2017/025016 Ceased WO2018061396A1 (fr) 2016-09-30 2017-07-07 Produit forgé, traité thermiquement en acier de cémentation

Family Applications After (1)

Application Number Title Priority Date Filing Date
PCT/JP2017/025016 Ceased WO2018061396A1 (fr) 2016-09-30 2017-07-07 Produit forgé, traité thermiquement en acier de cémentation

Country Status (1)

Country Link
WO (2) WO2018061197A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2019183266A (ja) * 2018-03-30 2019-10-24 株式会社神戸製鋼所 肌焼用鋼

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP7010320B2 (ja) * 2020-03-17 2022-02-10 愛知製鋼株式会社 真空浸炭用粗形材及びその製造方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1999005333A1 (fr) * 1997-07-22 1999-02-04 Nippon Steel Corporation Acier cemente particulierement capable d'empecher la recristallisation secondaire des particules pendant la cementation, procede de fabrication, et matiere brute formee pour pieces cementees
JP2004204263A (ja) * 2002-12-24 2004-07-22 Nippon Steel Corp 冷間加工性と浸炭時の粗大粒防止特性に優れた肌焼用鋼材とその製造方法
JP2005133153A (ja) * 2003-10-30 2005-05-26 Kobe Steel Ltd 冷間鍛造性及び肌焼処理時の耐粗粒化特性に優れた肌焼用鋼及びその製造方法
JP2008189989A (ja) * 2007-02-05 2008-08-21 Sumitomo Metal Ind Ltd 高温浸炭用鋼材
WO2015098528A1 (fr) * 2013-12-24 2015-07-02 新日鐵住金株式会社 Matériau à base d'acier pour forgeage chaud, son procédé de fabrication et produit grossièrement façonné obtenu par forgeage à chaud du matériau à base d'acier
JP2015160967A (ja) * 2014-02-26 2015-09-07 愛知製鋼株式会社 減圧高温浸炭処理用鍛造部品及びその製造方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1999005333A1 (fr) * 1997-07-22 1999-02-04 Nippon Steel Corporation Acier cemente particulierement capable d'empecher la recristallisation secondaire des particules pendant la cementation, procede de fabrication, et matiere brute formee pour pieces cementees
JP2004204263A (ja) * 2002-12-24 2004-07-22 Nippon Steel Corp 冷間加工性と浸炭時の粗大粒防止特性に優れた肌焼用鋼材とその製造方法
JP2005133153A (ja) * 2003-10-30 2005-05-26 Kobe Steel Ltd 冷間鍛造性及び肌焼処理時の耐粗粒化特性に優れた肌焼用鋼及びその製造方法
JP2008189989A (ja) * 2007-02-05 2008-08-21 Sumitomo Metal Ind Ltd 高温浸炭用鋼材
WO2015098528A1 (fr) * 2013-12-24 2015-07-02 新日鐵住金株式会社 Matériau à base d'acier pour forgeage chaud, son procédé de fabrication et produit grossièrement façonné obtenu par forgeage à chaud du matériau à base d'acier
JP2015160967A (ja) * 2014-02-26 2015-09-07 愛知製鋼株式会社 減圧高温浸炭処理用鍛造部品及びその製造方法

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2019183266A (ja) * 2018-03-30 2019-10-24 株式会社神戸製鋼所 肌焼用鋼

Also Published As

Publication number Publication date
WO2018061396A1 (fr) 2018-04-05

Similar Documents

Publication Publication Date Title
JP4709944B2 (ja) 肌焼鋼、浸炭部品、及び肌焼鋼の製造方法
JP5639064B2 (ja) 浸炭窒化部材の製造方法
JP5842895B2 (ja) 浸炭鋼部材の製造方法
CN103443316B (zh) 表面硬化钢及其制造方法、以及使用表面硬化钢的机械构造零件
JP4956146B2 (ja) 鍛造性と結晶粒粗大化防止特性に優れた肌焼鋼およびその製造方法並びに浸炭部品
JP5338188B2 (ja) 合金工具鋼及びその製造方法
JP6182489B2 (ja) 優れた冷間鍛造性を有し、浸炭処理時の異常粒発生が抑制可能な肌焼鋼
JP5649886B2 (ja) 肌焼鋼およびその製造方法
JP5649887B2 (ja) 肌焼鋼およびその製造方法
EP3173500B1 (fr) Matériau d'outil de travail à chaud, procédé de fabrication d'outil de travail à chaud et outil de travail à chaud
JP6765551B2 (ja) はだ焼鋼の鍛造熱処理品
JP4617783B2 (ja) 高温浸炭用熱間鍛造部品の製造方法
WO2018061197A1 (fr) Produit forgé thermiquement traité en acier de cémentation
CN108138287A (zh) 机械结构用钢及高频淬火钢部件
JP5402711B2 (ja) 浸炭窒化層を有する鋼製品およびその製造方法
JP4528363B1 (ja) 冷間加工性、切削性、浸炭焼入れ後の疲労特性に優れた肌焼鋼及びその製造方法
JP4681160B2 (ja) 高温浸炭用鋼の製造方法及びその方法により製造された高温浸炭用鋼
JP4488228B2 (ja) 高周波焼入れ用鋼材
US20050205168A1 (en) Crankshaft
JP2005281857A (ja) ブローチ加工性に優れた窒化部品用素材及びその素材を用いた窒化部品の製造方法
JP6551225B2 (ja) 高周波焼入れ歯車
JP4997709B2 (ja) ブローチ加工性に優れた窒化部品用素材及びその製造方法
JP6752624B2 (ja) 浸炭用鋼の製造方法
CN114929916B (zh) 真空渗碳用坯材和其制造方法
JP2023004760A (ja) 歯車

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 16917747

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 16917747

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: JP