EP1681365A1 - Acier de cementation pour des composants fortement chargés - Google Patents

Acier de cementation pour des composants fortement chargés Download PDF

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Publication number
EP1681365A1
EP1681365A1 EP06450006A EP06450006A EP1681365A1 EP 1681365 A1 EP1681365 A1 EP 1681365A1 EP 06450006 A EP06450006 A EP 06450006A EP 06450006 A EP06450006 A EP 06450006A EP 1681365 A1 EP1681365 A1 EP 1681365A1
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EP
European Patent Office
Prior art keywords
weight
ppm
steel
content
gew
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.)
Granted
Application number
EP06450006A
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German (de)
English (en)
Other versions
EP1681365B1 (fr
Inventor
Oskar Kehrer
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.)
Magna Drivetrain AG and Co KG
Original Assignee
Magna Drivetrain AG and Co KG
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Publication of EP1681365A1 publication Critical patent/EP1681365A1/fr
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Publication of EP1681365B1 publication Critical patent/EP1681365B1/fr
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    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/28—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for plain shafts
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/613—Gases; Liquefied or solidified normally gaseous material

Definitions

  • the invention relates to a steel for case-hardened heavy-duty machine parts and to a method for producing a heavy-duty machine part and a heavy-duty machine part.
  • a transmission shaft of this kind is a central main component of a transmission, which is also exposed to extreme requirements. Such a shaft must absorb high shock-like moments, with a relatively small outer diameter. In addition, most are strong weakenings due to a notch effect, caused by oil longitudinal and transverse holes, grooves, etc., given.
  • Such insert steels have a C content of between 0.10 and 0.20% by weight, in addition to other alloying elements provided for hardenability, such as Cr, Mn, Ni, Mo and V, in some cases in high alloy contents.
  • the invention aims to avoid the above-mentioned disadvantages and difficulties and has set itself the task of creating a steel for case-hardened heavy-duty machine parts and a method for producing such heavy duty machine parts, which in addition to a high core strength even with larger wall thickness by case hardening to very high hardnesses in Surface area can be brought, and this at a negligible even for complicated machine parts delay.
  • a good mechanical machinability by machining should be given.
  • the steel itself should be inexpensive, by using inexpensive alloying elements and avoiding the very expensive alloying elements such as Mo, and also the contents of alloying elements should be as low as possible.
  • the steel according to the invention thus has a significantly higher C content compared to classic case-hardening steels, namely more than 0.20% by weight, whereas it is between 0.10 and 0.20% by weight for classic case-hardened steels.
  • This higher C content is usually realized only for tempered steels.
  • this higher C content achieves higher core strengths during case hardening, and on the other hand, the transition to the case-hardened layer-a carburized surface layer has a C content of 0.8% by weight-is not so abrupt, but rather there is a rather smooth continuous strength transition between the rim and the core.
  • the boron content is between 30 and 120 ppm, ideally between 35 and 60 ppm. Boron brings an extremely strong increase in hardenability and is available as an alloying element virtually "free of charge”.
  • the steel expediently has a C content before case hardening of between 0.26 and 0.30% by weight, and an Mn content of between 1.5 and 2% by weight.
  • the Si content is appropriate to limit to 0.15 to 0.25 wt.% (Also advantageous because of the lower edge oxidation for increased fatigue strength) ,
  • the Si content may be up to 0.4 wt.%.
  • the Cr content is preferably between 0.05 and 1.0 wt%, more preferably between 0.4 and 0.8 wt%, ideally at about 0.6 wt%. Cr increases hardenability, but is more expensive than Mn.
  • the sulfur content is advantageously limited to between 0.02 and 0.4% by weight, resulting in better machinability by machining.
  • This optimally balanced composition of the alloying elements has the surprising effect that the hardenability of the material is extremely high even under the mildest quenching conditions. Due to the novelty of this alloy, the hardenability is of course also in the latest regulations (SEP1664, June 2004, "Determination of formulas by multiple regression to calculate the hardenability in the stimulus quenching test from the chemical composition of steels" + supplementary sheet to the SEP1664) not calculable, but only to characterize by practical experiments.
  • the case hardening is expediently carried out in a temperature range between 880 and 1050 ° C., preferably between 900 and 950 ° C. during carburization with subsequent diffusion between 840 and 880 ° C., preferably at about 860 ° C., where a C is suitably used during case hardening Level of 0.7 to 1.2 wt.%, Preferably from 1.0 to 1.1 wt.% When carburizing and from 0.7 to 0.8 wt.% Is set when diffusing.
  • the curing is advantageously carried out starting from a temperature of about 850 to 910 ° C, preferably starting from about 860 ° C.
  • Subsequent tempering takes place over a temperature range of max. 200 ° C, preferably to a temperature of about 160 ° C, wherein advantageously the quenching extremely mild, preferably with a gas pressure of about 2-3 bar nitrogen or air, is performed.
  • Fig. 1 shows a transmission shaft in section, which was made of a steel according to the invention and case hardened.
  • Fig. 2 gives the hardness values HRC of a case-hardened steel according to the invention in comparison with various other case-hardened steels according to the prior art, wherein the illustrated spreading widths of the hardness bands should be given special attention.
  • Figures 3, 4 and 5 show further comparisons of the achievable hardness HRC between a steel according to the invention and various conventional steel grades.
  • Figs. 6 to 8 illustrate micrographs of the surface area of a machine part.
  • the transmission shaft 1 shown in Fig. 1 represents a machine part, which can be difficult to use hardened, especially since it has a very large length and highly divergent cross-sectional values. Such a part is prone to distortion and is difficult to straighten after case hardening.
  • an internal toothing 2 and an external toothing 3 various snap grooves 4, and grooves and holes 6 for oil supply, resulting notch effects that result in the use of conventional steels only a low dynamic load capacity.
  • a second gear shaft (shaft II) of the same chemical composition was made with a case hardening depth Eht620HV1 of about 0.7 mm, by carburizing at 900 ° C (due to the observance of the exact gear data), with carburization over 4.7 hours with a C level of 1.05%.
  • the subsequent diffusion was carried out at 860 ° C over a period of one hour with a C level of 0.75%.
  • Case hardening produced a very hard surface layer> 58 HRC for both gear shafts. Values ranged from 61 to 62 HRC. At the same time, a very high core strength of over 42 HRC was found, ranging from 46 to 48 HRC, despite a very mild high pressure gas quench with nitrogen quench media.
  • the following table shows the hardness values of the two shafts reached at different points, with the cuts 1, 2 and 3 from FIG. 1 as well as the surface hardness test points being able to be seen.
  • the surface hardness measuring points are noted with OH1, OH2 and OH3 in Fig. 1.
  • test bodies for the Jominy forehead quenching test according to ISO642 were also produced.
  • the steel according to the invention has a superiority after case hardening in comparison to previously used types of steel, above all at a greater distance from the end face.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Articles (AREA)
EP06450006A 2005-01-14 2006-01-12 Procédé de fabrication des composants fortement chargés Not-in-force EP1681365B1 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
AT0001105U AT8065U1 (de) 2005-01-14 2005-01-14 Stahl für einsatzgehärtete hochbeanspruchbare maschinenteile

Publications (2)

Publication Number Publication Date
EP1681365A1 true EP1681365A1 (fr) 2006-07-19
EP1681365B1 EP1681365B1 (fr) 2010-09-29

Family

ID=35406108

Family Applications (1)

Application Number Title Priority Date Filing Date
EP06450006A Not-in-force EP1681365B1 (fr) 2005-01-14 2006-01-12 Procédé de fabrication des composants fortement chargés

Country Status (3)

Country Link
EP (1) EP1681365B1 (fr)
AT (1) AT8065U1 (fr)
DE (1) DE502006007937D1 (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
ES2293837A1 (es) * 2006-07-31 2008-03-16 Sidenor Industrial, S.L. Proceso de fabricacion de un acero, y acero obtenido en este proceso.
CN113981316A (zh) * 2021-10-27 2022-01-28 温州天和汽车部件有限公司 一种高精度链轮冷挤压工艺

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20210371947A1 (en) * 2017-11-15 2021-12-02 Sidenor Investigacion Y Desarrollo, S.A. Alloyed steel and quenched and tempered steel

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5178688A (en) * 1991-11-30 1993-01-12 Samsung Heavy Industries Co., Ltd. Carburized boron steels for gears
JPH0892690A (ja) * 1994-09-27 1996-04-09 Sumitomo Metal Ind Ltd 耐疲労特性に優れた浸炭部品およびその製造方法
JPH08311607A (ja) * 1995-05-16 1996-11-26 Sumitomo Metal Ind Ltd 歯元曲げ強度に優れた低歪浸炭歯車およびその製造方法

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5178688A (en) * 1991-11-30 1993-01-12 Samsung Heavy Industries Co., Ltd. Carburized boron steels for gears
JPH0892690A (ja) * 1994-09-27 1996-04-09 Sumitomo Metal Ind Ltd 耐疲労特性に優れた浸炭部品およびその製造方法
JPH08311607A (ja) * 1995-05-16 1996-11-26 Sumitomo Metal Ind Ltd 歯元曲げ強度に優れた低歪浸炭歯車およびその製造方法

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 1996, no. 08 30 August 1996 (1996-08-30) *
PATENT ABSTRACTS OF JAPAN vol. 1997, no. 03 31 March 1997 (1997-03-31) *

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
ES2293837A1 (es) * 2006-07-31 2008-03-16 Sidenor Industrial, S.L. Proceso de fabricacion de un acero, y acero obtenido en este proceso.
CN113981316A (zh) * 2021-10-27 2022-01-28 温州天和汽车部件有限公司 一种高精度链轮冷挤压工艺
CN113981316B (zh) * 2021-10-27 2022-07-19 温州天和汽车部件有限公司 一种高精度链轮冷挤压工艺

Also Published As

Publication number Publication date
DE502006007937D1 (de) 2010-11-11
EP1681365B1 (fr) 2010-09-29
AT8065U1 (de) 2006-01-15

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