EP1044287A1 - Acier de nitruration, procede pour son obtention et pieces formees avec cet acier - Google Patents
Acier de nitruration, procede pour son obtention et pieces formees avec cet acierInfo
- Publication number
- EP1044287A1 EP1044287A1 EP99946245A EP99946245A EP1044287A1 EP 1044287 A1 EP1044287 A1 EP 1044287A1 EP 99946245 A EP99946245 A EP 99946245A EP 99946245 A EP99946245 A EP 99946245A EP 1044287 A1 EP1044287 A1 EP 1044287A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- nitriding
- steel
- weight
- temperature
- composition
- 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
Links
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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- 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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- 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
- C23C8/24—Nitriding
- C23C8/26—Nitriding of ferrous surfaces
Definitions
- the present invention relates to a composition of nitriding steel, parts formed with this steel, as well as a method for manufacturing parts produced in this steel.
- Nitriding is a thermochemical treatment of surface hardening by introducing nitrogen into the steel. This process is used in all fields of mechanics and is used in particular to manufacture gears, splines, transmission shafts, cam shafts, heat engine distribution parts, pump bodies, injector bodies , crankshafts, extrusion screws, hydraulic distributors, guide rails, bearing cages, control gauges and shaping tool parts.
- Nitriding generally takes place in a temperature range of about 450 to 600 ° C, temperatures for which the diffusion of nitrogen is relatively slow.
- Conventional nitriding steels such as 40CrAIMo6.12, 25NiAICr14.12, 30CrMo12 or 32CrMoV13
- the main object of the present invention is therefore to provide a nitriding steel composition making it possible to conserve the tensile, resilience, toughness, hardenability, fatigue, and surface hardness properties of the nitrided layers of nitriding steels.
- type 32CrMoV13 while increasing the nitrogen diffusion kinetics, to allow either greater depths of nitriding, or reduced nitriding times.
- a first subject of the invention is thus a composition of nitriding steel, comprising, expressed in% by weight,
- the sulfur is preferably limited to 0.015% and the phosphorus to 0.020% by weight.
- Elements such as calcium, cerium, titanium, zirconium, niobium which are used either to deoxidize the steel or to refine the grain size are preferably limited to 0.1% by weight each.
- the carbon range is 0.2-0.4% by weight in order to obtain, after quenching and returning to a temperature compatible with subsequent nitriding, a maximum tensile strength in the range from 900 to 1500 MPa. Tight carbon forks are also interesting:
- the carbon also contributes to the quenchability of the alloy as well as to its resistance to tempering and to its resistance to softening during the nitriding cycle.
- the silicon must be limited because it leads, during nitriding, to the precipitation of carbonitrides which participate little in hardening, but reduce the rate of diffusion of nitrogen. For these reasons, it is limited to 0.5% by weight at most, and preferably 0.35% by weight. Chromium is one of the predominant elements for obtaining the characteristics of the nitrided layer, but it leads to a significant precipitation of nitrogen in the form of carbonitrides, which reduces the rate of diffusion of nitrogen in the nitrided layer. Chromium also has a beneficial influence on the hardenability of the undercoat. These considerations lead to limiting the chromium content to 0.8-2% by weight, preferably to 1.1-1.8% by weight.
- the lowering of the chromium content induces a reduction in hardening during nitriding, which is compensated by an increase in the molybdenum and vanadium contents, as well as by the addition of aluminum.
- the molybdenum and vanadium elements increase the resistance to tempering of the steel and limit its softening during nitriding.
- Their content must be limited because too large a quantity would lead to embrittlement of the steel underlayment. The contents are therefore limited to 0.6-2% by weight for the molybdenum, to at most 0.5% by weight for the vanadium, and to 0.05% -0.4% by weight for the aluminum. Tighter ranges are preferred: 0.8-1.5% by weight for the molybdenum, 0.1-0.4% by weight for vanadium and 0.1-0.3% by weight for aluminum.
- a second object of the invention is a process for manufacturing treated and nitrided parts, comprising the following operations: a - constitution of a filler intended to obtain a composition in accordance with the present invention, as described above, b - preparation of said charge in an arc furnace, c - heating and hot transformation of the ingot, d - heat treatment for homogenizing the structure and refining the grain, e - heat treatment for use, and f - nitriding.
- the steel according to the invention can be obtained by conventional production techniques, but to obtain better results in resilience, tenacity and fatigue it is preferable to carry out a reflow by consumable electrode either under slag (ESR) or under reduced pressure
- VIM reduced pressure
- thermomechanical transformations aimed at giving the product produced in this alloy a sufficient degree of wrinkling which will be preferred greater than or equal to 3 Lower working rates may be allowed for large parts.
- thermomechanical transformations are based on conventional procedures, such as rolling, forging, stamping or spinning.
- step d of the method according to the invention Processed products can simply be softened at a temperature below the point critical (ACi), or annealed at a temperature above the critical point (ACi), which then assumes a sufficiently slow start of cooling.
- ACi point critical
- ACi critical point
- the critical point temperature (ACi) is generally in the range from 700 ° C to 790 ° C, while the critical point temperature (AC 3 ) is generally in the range from 800 ° C at 890 ° C.
- the products are then quenched and returned in the form of a rolled bar, forged or stamped blank, pre-machined parts.
- the quenching takes place from an austenitization temperature above the critical point (AC 3 ), in the range from 900 to 1000 ° C., for example.
- the quenching fluid is adjusted, in a conventional manner, according to the section of the products.
- the tempering is then carried out at a temperature adjusted as a function of the mechanical characteristics sought for the core, in the range of approximately 550 ° C. to approximately 750 ° C.
- the choice must take into account the temperature at which nitriding will take place.
- a tempering temperature at least 30 ° C higher than the nitriding temperature is preferred. In certain particular cases, nitriding can take the place of income.
- Nitriding, step f of the process according to the invention is then carried out on a finished or almost finished workpiece. The time and temperature parameters are to be set according to the compromise sought in surface hardness, depth and microstructure for the layer.
- a third object of the invention consists of the treated and nitrided parts made with the steel according to the invention. These parts can advantageously be manufactured by means of the manufacturing method according to the invention, but also by any other method chosen according to the final application.
- the classic steel chosen as a comparison element is steel
- the nitriding step it was systematically carried out with the gaseous nitriding process using ammonia.
- HV 50 Vickers hardness under a load of 50 kg
- HRC Rockwell C hardness
- KV impact energy in impact bending on V-notch test piece
- KCU impact energy in impact bending on U-shaped test piece
- FIG. 1 represents the hardness profile of two samples, the preparation of which is described in example 1,
- FIG. 2 represents the hardness profile of two samples, the preparation of which is described in Example 2,
- FIG. 3 represents the hardness profile of two samples, the preparation of which is described in Example 3
- FIG. 4 represents the hardness profile of two samples, the preparation of which is described in Example 4,
- FIG. 5 represents the hardness profile of two samples, the preparation of which is described in Example 5,
- FIG. 6 represents the hardness profile of two samples, the preparation of which is described in Example 6,
- FIG. 7 represents the hardness profile of two samples, the preparation of which is described in Example 7,
- FIG. 8 represents the hardness profile of two samples, the preparation of which is described in Example 8
- FIG. 9 represents the hardness profile of two samples, the preparation of which is described in Example 9.
- a 35 kg ingot was produced in the chemical composition indicated in percentage by weight below, in accordance with the indications of the present invention:
- This ingot was produced by arc fusion, it was then homogenized at high temperature (1100 ° C) to obtain a uniform structure, then it was forged. The forged products were slowly cooled in the oven. They have been standardized in order to dissolve the carbides, to homogenize the austenitic structure and to refine the grain. Bars from this ingot were austenitized at 940 ° C, quenched in oil, then returned to a temperature of 650 ° C.
- This profile shows that the steel according to the present invention has, for the same nitriding cycle, a surface hardness equivalent to that of 32CrMoV13 steel and a significantly greater nitrided depth.
- a 35 kg ingot was produced in the chemical composition indicated in percentage by weight below, in accordance with the indications of the present invention:
- This ingot was produced by arc fusion, it was then homogenized at high temperature (1100 ° C) to obtain a uniform structure, then it was forged.
- the forged products were slowly cooled in the oven. They have been standardized in order to dissolve the carbides, to homogenize the austenitic structure and to refine the grain.
- This profile shows that the steel according to the present invention has, for the same nitriding cycle, a surface hardness equivalent to that of 32CrMoV13 steel and a significantly greater nitrided depth.
- a 35 kg ingot was produced in the chemical composition indicated in percentage by weight below, in accordance with the indications of the present invention:
- Bars from this ingot were austenitized at 940 ° C, quenched in oil, then returned to a temperature of 650 ° C.
- This profile shows that the steel according to the present invention has, for the same nitriding cycle, a surface hardness equivalent to that of 32CrMoV13 steel and a significantly greater nitrided depth.
- a 35 kg ingot was produced in the chemical composition indicated in percentage by weight below, in accordance with the indications of the present invention:
- This ingot was produced by arc fusion, it was then homogenized at high temperature (1100 ° C) to obtain a uniform structure, then it was forged.
- the forged products were slowly cooled in the oven. They have been standardized in order to dissolve the carbides, to homogenize the austenitic structure and to refine the grain.
- Bars from this ingot were austenitized at 940 ° C, quenched in oil, then returned to a temperature of 650 ° C.
- This profile shows that the steel according to the present invention has, for the same nitriding cycle, a surface hardness equivalent to that of 32CrMoV13 steel and a significantly greater nitrided depth.
- a 35 kg ingot was produced in the chemical composition indicated in percentage by weight below, in accordance with the indications of the present invention: C 0.38%
- This ingot was produced by arc fusion, it was then homogenized at high temperature (1100 ° C) to obtain a uniform structure, then it was forged.
- the forged products were slowly cooled in the oven. They have been standardized in order to dissolve the carbides, to homogenize the austenitic structure and to refine the grain.
- Bars from this ingot were austenitized at 940 ° C, quenched in oil, then returned to a temperature of 650 ° C.
- a 35 kg ingot was produced in the chemical composition indicated in percentage by weight below, in accordance with the indications of the present invention:
- This ingot was produced by arc fusion, it was then homogenized at high temperature (1100 ° C) to obtain a uniform structure, then it was forged.
- the forged products were slowly cooled in the oven. They have been standardized in order to dissolve the carbides, to homogenize the austenitic structure and to refine the grain.
- Bars from this ingot were austenitized at 940 ° C, quenched in oil, then returned to a temperature of 650 ° C.
- This profile shows that the steel according to the present invention has, for the same nitriding cycle, a surface hardness equivalent to that of 32CrMoV13 steel and a significantly greater nitrided depth.
- a 35 kg ingot was produced in the chemical composition indicated in percentage by weight below, in accordance with the indications of the present invention:
- This ingot was produced by arc fusion, it was then homogenized at high temperature (1100 ° C) to obtain a uniform structure, then it was forged.
- the forged products were slowly cooled in the oven. They have been standardized in order to dissolve the carbides, to homogenize the austenitic structure and to refine the grain.
- This profile shows that the steel according to the present invention has, for the same nitriding cycle, a surface hardness equivalent to that of 32CrMoV13 steel and a significantly greater nitrided depth.
- a 35 kg ingot was produced in the chemical composition indicated in percentage by weight below, in accordance with the indications of the present invention:
- Bars from this ingot were austenitized at 940 ° C, quenched in oil, then returned to a temperature of 650 ° C.
- This profile shows that the steel according to the present invention has, for the same nitriding cycle, a surface hardness equivalent to that of 32CrMoV13 steel and a significantly greater nitrided depth.
- This ingot was obtained by vacuum fusion and then remelting by consumable electrode, it was then reheated to high temperature (1100 ° C) in order to homogenize the structure, then it was rolled to result in cylindrical bars with a diameter of 100 mm. These bars have undergone a normalization treatment in order to dissolve the carbides, homogenize the austenitic structure and refine the grain size.
- Samples taken from these bars were austenitized at 940 ° C, quenched in oil and returned to 650 ° C.
- FIG. 9 also makes it possible to compare the hardness profiles obtained after nitriding with this steel and with a 32CrMoV13 steel.
- the depth of the hardness gradient makes it possible to measure the performance of a steel according to the invention in terms of kinetics of nitriding.
- This depth is conventionally defined in Europe by measuring the depth at which the hardness is equal to that of the core + 100 HV (Vickers hardness). In the United States, the convention is to define the depth at which the hardness is equal to 50 HRC (i.e. 513 HV, value obtained by conversion according to ASTM E140).
- the parts manufactured using the steel according to the invention can be, in particular, bars, sheets, forged or stamped blanks, tubes or wires.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
- Catalysts (AREA)
- Ceramic Products (AREA)
- Saccharide Compounds (AREA)
- Treatment Of Steel In Its Molten State (AREA)
Description
Claims
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR9812209 | 1998-09-30 | ||
FR9812209A FR2783840B1 (fr) | 1998-09-30 | 1998-09-30 | Acier permettant des cinetiques de nitruration elevees, procede pour son obtention et pieces formees avec cet acier |
PCT/FR1999/002297 WO2000018975A1 (fr) | 1998-09-30 | 1999-09-28 | Acier de nitruration, procede pour son obtention et pieces formees avec cet acier |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1044287A1 true EP1044287A1 (fr) | 2000-10-18 |
EP1044287B1 EP1044287B1 (fr) | 2011-11-02 |
Family
ID=9531010
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP99946245A Expired - Lifetime EP1044287B1 (fr) | 1998-09-30 | 1999-09-28 | Procédé de fabrication de pieces nitrurées |
Country Status (7)
Country | Link |
---|---|
EP (1) | EP1044287B1 (fr) |
AT (1) | ATE531832T1 (fr) |
CA (1) | CA2312034C (fr) |
DK (1) | DK1044287T3 (fr) |
ES (1) | ES2374261T3 (fr) |
FR (1) | FR2783840B1 (fr) |
WO (1) | WO2000018975A1 (fr) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2013087379A1 (fr) * | 2011-12-12 | 2013-06-20 | Aktiebolaget Skf | Composant de roulement |
Families Citing this family (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP4142853B2 (ja) | 2001-03-22 | 2008-09-03 | 新日本製鐵株式会社 | 耐遅れ破壊特性に優れた高力ボルト |
FR2884879B1 (fr) * | 2005-04-22 | 2007-08-03 | Stephanois Rech Mec | Couple d'organes de guidage dont l'un est en acier particulier conduisant a des performances ameliorees. |
DE102006025008B4 (de) | 2006-05-30 | 2022-09-15 | Schaeffler Technologies AG & Co. KG | Verfahren zum Härten von Laufflächen von Wälzlagerkomponenten |
Family Cites Families (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0756043B2 (ja) * | 1988-09-27 | 1995-06-14 | マツダ株式会社 | 鋼部材の製造方法 |
JPH0445244A (ja) * | 1990-06-09 | 1992-02-14 | Aichi Steel Works Ltd | 疲労強度の優れた迅速窒化用鋼 |
JPH073392A (ja) * | 1993-06-18 | 1995-01-06 | Nkk Corp | 窒化用鋼 |
JP2885061B2 (ja) * | 1994-04-20 | 1999-04-19 | 日本鋼管株式会社 | 疲労特性に優れた窒化鋼部材の製造方法 |
JPH0849058A (ja) * | 1994-08-03 | 1996-02-20 | Nkk Corp | 熱処理歪みの少ない耐摩耗窒化鋼部材の製造方法 |
JPH08176732A (ja) * | 1994-12-27 | 1996-07-09 | Nkk Corp | 被削性の優れた窒化用鋼 |
JP3069256B2 (ja) * | 1995-01-12 | 2000-07-24 | 住友金属工業株式会社 | 靭性に優れた窒化用鋼 |
DK0828007T3 (da) * | 1995-05-15 | 2002-02-25 | Sumitomo Metal Ind | Fremgangsmåde til fremstilling af sømløst stålrør med høj styrke og fremragende sulfidspændingsrevnebestandighed |
-
1998
- 1998-09-30 FR FR9812209A patent/FR2783840B1/fr not_active Expired - Lifetime
-
1999
- 1999-09-28 ES ES99946245T patent/ES2374261T3/es not_active Expired - Lifetime
- 1999-09-28 DK DK99946245.0T patent/DK1044287T3/da active
- 1999-09-28 WO PCT/FR1999/002297 patent/WO2000018975A1/fr active Application Filing
- 1999-09-28 AT AT99946245T patent/ATE531832T1/de active
- 1999-09-28 EP EP99946245A patent/EP1044287B1/fr not_active Expired - Lifetime
- 1999-09-28 CA CA2312034A patent/CA2312034C/fr not_active Expired - Lifetime
Non-Patent Citations (1)
Title |
---|
See references of WO0018975A1 * |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2013087379A1 (fr) * | 2011-12-12 | 2013-06-20 | Aktiebolaget Skf | Composant de roulement |
Also Published As
Publication number | Publication date |
---|---|
EP1044287B1 (fr) | 2011-11-02 |
CA2312034C (fr) | 2010-06-01 |
FR2783840B1 (fr) | 2000-11-10 |
CA2312034A1 (fr) | 2000-04-06 |
WO2000018975A1 (fr) | 2000-04-06 |
ATE531832T1 (de) | 2011-11-15 |
DK1044287T3 (da) | 2011-12-12 |
ES2374261T3 (es) | 2012-02-15 |
FR2783840A1 (fr) | 2000-03-31 |
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