Classifications

• • 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
  • C21D1/18—Hardening; Quenching with or without subsequent tempering
• • 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
  • 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
  • C21D1/06—Surface hardening
  • C21D1/09—Surface hardening by direct application of electrical or wave energy; by particle radiation
  • C21D1/10—Surface hardening by direct application of electrical or wave energy; by particle radiation by electric induction
• • 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
  • C21D1/26—Methods of annealing
• • 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
  • C21D1/34—Methods of heating
  • C21D1/38—Heating by cathodic discharges
• • 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
  • C21D1/78—Combined heat-treatments not provided for above
• • 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
  • 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
• • 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
  • C23C8/36—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 using ionised gases, e.g. ionitriding
  • C23C8/38—Treatment of ferrous surfaces
• • 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
  • C23C8/40—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 liquids, e.g. salt baths, liquid suspensions
  • C23C8/52—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 liquids, e.g. salt baths, liquid suspensions more than one element being applied in one step
  • C23C8/54—Carbo-nitriding
  • C23C8/56—Carbo-nitriding of ferrous surfaces
• • 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
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/008—Martensite
• • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
  • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
  • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
  • Y02P10/00—Technologies related to metal processing
  • Y02P10/25—Process efficiency

Definitions

• the field of the invention is that of the surface treatment of ferrous metal parts, in particular very low or low alloy steel.
• the parts can receive one or more treatments making it possible to improve some of their performances, among which the frictional properties, the wear resistance, the fatigue resistance, the chipping resistance, the resistance. corrosion, etc.
• document WO2011013362A1 describes a method of treating a part, comprising a nitriding operation, a coating operation with a chemical conversion film (sol-gel), and an induction hardening operation.
• a nitriding operation comprising a nitriding operation, a coating operation with a chemical conversion film (sol-gel), and an induction hardening operation.
• the aim of the present invention is to remedy the above drawbacks, while maintaining a good compromise between the different properties of the part.
• the invention relates to a process for treating a piece of ferrous metal, comprising:
• a nitriding operation forming on the part a combination layer having a thickness between 5 ⁇ m and 30 ⁇ m, and a diffusion zone arranged under and in contact with the combination layer having a thickness between 100 ⁇ m and 500 ⁇ m; then - a high-frequency induction hardening operation of the part, to an induction depth greater than or equal to 0.5 mm, causing hardening of the part providing said part:
• the method of the invention makes it possible to obtain a part exhibiting both high resistance to wear by abrasion and adhesion, improved friction properties and resistance to chipping, as well as good corrosion resistance. .
• the method of the invention is also simpler to implement and less expensive than the methods of the prior art because it saves the arrangement of a protective film of the combination layer, as well as the possible removal of said layer. protective film.
• the protective film can be of any type suitable for preventing degradation of the combination layer during hardening by high frequency induction, this degradation being able to manifest itself by chipping, cracking, or fracturing of the combination layer.
• the protective film can be a sol-gel film. Therefore, the high-frequency induction hardening operation is performed without a sol-gel film.
• the treatment process according to the invention has the following different characteristics taken alone or according to their technically possible combinations: the nitriding operation is carried out with gas, or by plasma, or by molten salts; the nitriding operation is carried out at a temperature between 500 ° C and 630 ° C, for a period of between 15 minutes and 3 hours; the induction hardening operation is not followed by a tempering operation; the workpiece high-frequency induction hardening operation is carried out so as to retain ferrite in the workpiece between the diffusion zone / combination layer interface and a depth of 500 ⁇ m, preferably between the zone interface diffusion / combination layer and a depth of 300 ⁇ m.
• the diffusion zone / combination layer interface means the contact surface between the diffusion zone and the overlying combination layer. Quenching is quick and does not not completely transform the part's ferrite into martensite over its processing depth, so that ferrite remains over the depth treated by HF quenching at the end of the process.
• the depth of 500 ⁇ m corresponds to an induction depth where hardening and / or changes in the metallurgical structure of the part are observed; the high-frequency induction hardening operation of the part is carried out so as to have a residual ferrite level in the part, between the diffusion zone / combination layer interface and a depth of 500 ⁇ m, between 1% and 50% by volume, preferably between 1% and 30%, and more preferably between 5% and 30%.
• the level of residual ferrite is volume, and corresponds to the ratio of the volume of ferrite to the volume of the rest of the part in the zone considered; the high-frequency induction hardening operation of the part is carried out so as to have a residual ferrite level in the part, between the diffusion zone / combination layer interface and a depth of 500 ⁇ m, between 5% and 20% by volume, preferably between 5% and 15%; the method comprises an impregnation step subsequent to the high-frequency induction hardening operation. If a tempering step is performed, impregnation is performed after tempering. It can be done for example by soaking or by spraying.
• Impregnation protects the part because it makes it possible to delay the onset of corrosion, reduce the corrosion rate and thus increase the life of the part; the process provides the part with corrosion resistance greater than 80 hours during a neutral salt spray test.
• Corrosion resistance is measured by a neutral salt spray test, sometimes also called a standard salt spray, according to EN ISO 9227; the high-frequency induction hardening operation is carried out with the following parameters:
• This dual condition on frequency and linear energy makes it possible to obtain a ferrous metal part whose mechanical properties are greatly improved compared to parts of the state of the art, in particular resistance to wear by abrasion and adhesion, friction, resistance to chipping, while maintaining good corrosion resistance.
• the frequency and linear energy are adjusted according to the morphology of the part, for example its diameter; the high-frequency induction hardening operation is carried out with a running speed of between 5 and 40 mm / s.
• the invention also relates to a part made of ferrous metal, comprising a combination layer having a thickness between 5 ⁇ m and 30 ⁇ m, and a diffusion zone arranged under and in contact with the combination layer, having a thickness between 100 pm and 500 pm, said part having:
• a hardness of the part greater than or equal to 500 HV0.05 at a depth of 500 ⁇ m, said part comprising ferrite and martensite between the diffusion zone / combination layer interface and a depth of 500 ⁇ m.
• the ferrous metal part according to the invention has the following different characteristics taken alone or according to their technically possible combinations: the hardness of the part at a depth of 0.5 mm is greater than or equal to a hardness of core + 100 HV0.05; the hardness of the part at a depth of 0.25 mm is greater than or equal to a core hardness + 350 HV0.05; the part is made of very low alloy steel, of the C10-C70 family, with a manganese content of less than 1%. Under these conditions, the steel does not exhibit any significant addition element, that is to say an element which would exceed 5% by mass relative to the total mass of the steel.
• the part is made of C45 grade steel.
• grade designates a specific steel in a family. In particular, this is the C45 grade chosen from the C10 to C70 family of steels; the part is made of low alloy steel, with no addition element exceeding 5% by mass.
• the part is made of 31CrMo4 grade steel; the part comprises ferrite and martensite between the diffusion zone / combination layer interface and a depth of 300 ⁇ m; the part comprises a level of ferrite, between the diffusion zone / combination layer interface and a depth of 500 ⁇ m, between 1% and 50% by volume, preferably between 1% and 30%, and more preferably between 5% and 30%; the part comprises a level of ferrite, between the diffusion zone / combination layer interface and a depth of 500 ⁇ m, between 5% and 20% by volume, preferably between 5% and 15%; the part exhibits a corrosion resistance greater than 80 hours in a neutral salt spray test.
• thickness is understood to mean the distance between the upper limit and the lower limit of a layer or a given area within the piece of ferrous metal. The thickness is perpendicular to the average surface of said upper and lower limits.
• depth designates the distance between the surface of the part, also called the free surface, and a given point within the part. The depth is perpendicular to the mean surface of the free surface.
• a hardness of the diffusion zone greater than or equal to 500 HV0.05 at a depth of 500 ⁇ m means that at a distance of 500 ⁇ m within the part, counted from the free surface of the part. part, the hardness of the diffusion zone is greater than or equal to 500 HV0.05.
• nitriding In a manner known per se, nitriding consists of immersing a piece of ferrous metal in a medium liable to give up nitrogen.
• nitriding includes nitrocarburizing, which is a variant of nitriding, in which carbon enters the part in addition to nitrogen.
• the ARCOR process described in the remainder of this text is a preferred example of a nitrocarburizing process.
• the diffusion zone is arranged under the combination layer, and extends towards the core of the part (away from the free surface) from said combination layer.
• the combination layer for its part can be on the surface of the part or at a given depth.
• An induction depth greater than or equal to 0.5 mm means that the hardening and / or changes in the metallurgical structure of the part, caused by the induction hardening step, extend from the surface of the part to 'to a depth of at least 0.5 mm. Beyond a certain depth, the thermal effect gradually diminishes until there is no longer any measurable effect on the microstructure and hardness of the part.
• the high-frequency induction hardening operation provides a hardness of the part greater than or equal to 500 HV0.05 at a depth of 500 ⁇ m, and preferably a corrosion resistance greater than 80 hours when tested at. standard salt spray.
• the hardening by high-frequency induction according to the invention makes it possible to reinforce the mechanical characteristics, in particular the hardness, of the part nitrided beforehand, while retaining the combination layer.
• the corrosion resistance of the parts is maintained without resorting to an additional device such as, for example, a sol-gel film or a paint. Without a sol-gel film, processing costs are reduced.
• FIG. 1 is a graph illustrating the hardness profile of two parts, respectively compliant (ARCOR FLASH, that is to say ARCOR nitriding treatment followed by high frequency induction hardening) and not in accordance with the invention ( ARCOR alone, without high frequency induction hardening).
• Figure 2 is a table describing a series of tests carried out on steel parts, in order to characterize the process according to the invention.
• Figure 3 is a graph illustrating a series of tests corresponding to the table in Figure 2.
• FIG. 4 is a micrograph of a part treated by the method according to the invention.
• Figure 5 is a close-up view of Figure 4.
• Figure 6 is a micrograph of a part treated according to the prior art (ARCOR treatment followed by induction hardening according to the prior art).
• Figure 7 is a micrograph of a part treated after ARCOR treatment, without induction hardening.
• Figure 8 is a micrograph of a ferrous metal part according to the invention (ARCOR FLASH treatment).
• FIG. 9 is an assembly of a micrograph of a ferrous metal part according to the invention and of a hardness profile obtained by measurement on this same part.
• FIG. 10 is a graph illustrating the evolution of the friction coefficient of rings, for a ring in accordance with the invention (ARCOR FLASH treatment) and a ring of the state of the art (ARCOR treatment alone).
• FIG. 11 is a photograph of a ferrous metal part having undergone an ARCOR treatment alone.
• Figure 12 is a photograph of a ferrous metal part according to the invention, having undergone an ARCOR FLASH treatment (ARCOR nitriding followed by high frequency induction hardening).
• ARCOR FLASH treatment ARCOR nitriding followed by high frequency induction hardening
• Figure 13 is a close-up view of the micrograph of Figure 4, centered on the induction layer.
• the inventors' approach was to carry out several series of tests using different treatments of a ferrous metal part.
• the ARCOR nitrocarburizing treatment (trademark registered by the Applicant) provides, from the surface to the core of the part, a combination layer 2 and a diffusion zone 3 juxtaposed (see FIG. 4).
• the combination layer 2 typically has a thickness of about 20 ⁇ m, while the diffusion zone 3 typically has a thickness of a few tens or hundreds of microns, for example 300 ⁇ m.
• High frequency hardening (frequency> 20 kHz) provides a martensitic structure on the surface of the part, on an induction layer generally having a depth of around 1 mm.
• the induction hardening extends from the surface of the part to a depth of the order of 1 mm, and is superimposed on the hardening profile already obtained by the nitriding.
• the induction layer comprises Fe (a ') martensite resulting from the transformation of Fe (a) ferrite, as well as the remaining untransformed Fe (a) ferrite, and offers a significant hardness, admitted as very favorable to resistance to abrasive wear and fatigue.
• the combination layer 2 offers, among other things, good frictional properties, high adhesive wear resistance and good corrosion resistance.
• the diffusion zone 3 offers a hardness gradient, between the combination layer 2 and the base material 1 located under the diffusion zone 3, favorable to a certain wear resistance (abrasive and adhesive) and a resistance to the tired.
• HF FLASH quenching makes it possible to minimize or even eliminate the degradation of the ARCOR combination layer 2 (oxidation or spalling which induces the loss of corrosion resistance properties and the tribological properties associated with the combination layer 2).
• part P retains its basic properties provided by ARCOR.
• HF FLASH quenching increases the hardness below combination layer 2, as well as the depth of hardening.
• Figure 1 is a graph for comparing the hardness profile of two parts, including a part receiving ARCOR treatment alone (Series 1) and a part receiving ARCOR FLASH treatment according to the invention (Series 5).
• the ARCOR FLASH treatment increases the hardness below the combination layer 2, especially in the diffusion zone, as well as the depth of cure.
• the diffusion zone 3 has a thickness of between 400 ⁇ m and 500 ⁇ m and the induction depth is approximately 1 mm.
• Figure 2 is a table describing a series of tests carried out on steel parts, in order to characterize the ARCOR FLASH treatment process according to the invention.
• the parts are steel bars with a diameter of 38 mm, having received an ARCOR treatment creating a combination layer with a thickness between 15 and 20 ⁇ m.
• the E1-E9 tests are carried out on C45 steel bars, the E10 and E11 tests on C10 steel bars, and the E12 test on a C70 steel bar and the E13 test on a 42CD4 steel bar.
• the tests consist of high-frequency induction hardening operations, carried out with variable parameters.
• the travel speed is that of the mobile magnetic inductor in translation along the part.
• test E2 also allow satisfactory results to be obtained with a C70 steel.
• Figure 3 is a graph showing the results of tests E1-E9 of Figure 2, performed on C45 steel bars.
• Linear energy is defined as being the power of the induction reduced to the running speed of the parts P during the induction. This quantity is linked to the geometry of the P parts processed. Another more general quantity could be a surface power density applied over a certain time, that is to say the power of the induction divided by the surface area of the part absorbing the induction, and divided by the running speed. It would thus be possible, from optimal hardening parameters for a part of a first dimension, to easily find the optimal hardening parameters for a part of a second dimension (for example of larger diameter), the other parameters being otherwise equal (same material, same nitriding).
• the hardness of the diffusion zone at a depth of 0.25 mm is greater than or equal to a hardness core + 350 HV0.05, and the hardness of the diffusion zone at a depth of 0.5 mm is greater than or equal to the core hardness + 100 HV0.05.
• the treatment according to the invention is therefore effective up to a great depth in the diffusion zone.
• FIGS. 4 and 5 are micrographs of a part P in C45 steel having received the ARCOR FLASH treatment (ARCOR + HF induction hardening, according to the invention) with a combination layer 2 of 18 ⁇ m, a diffusion zone 3 of about 300pm and an induction depth of about 0.5mm.
• ARCOR FLASH treatment ARCOR + HF induction hardening, according to the invention
• Part P comprises a steel substrate 1, an induction layer 4, a combination layer 2 and diffusion zone 3.
• An aluminum foil 5 and a coating 6 have been added in order to make the cut necessary to make micrography.
• the segment [AB] represents the distance (the thickness) between an average surface of the combination layer 2 (interface between the diffusion zone 3 and the combination layer 2), and an average surface of the substrate steel 1.
• the combination layer 2 and the diffusion zone 3 are here obtained by ARCOR nitrocarburizing.
• the induction layer 4 is obtained by high-frequency induction. It is composed of fine martensite Fe (a ’) and ferrite Fe (a).
• FIG. 5 clearly shows the presence of Fe (a) ferrite remaining in the quenching zone of the part obtained at the end of the process, after quenching. It is a microstructure which conforms to the invention.
• Figure 6 illustrates a micrograph of a steel that was nitrided and then received a conventional HF quenching: all the Fe (a) ferrite was transformed into Fe (a ’) martensite during the quenching. There is therefore no longer any ferrite left in the treated area. This microstructure is therefore not in accordance with the invention.
• FIG. 7 illustrates a part made of ferrous metal having received an ARCOR nitrocarburizing alone (without quenching), and FIG. 8 illustrates a part according to the invention, therefore having received a nitrocarburizing then an HF quenching (ARCOR + hardening by HF induction, according to invention).
• the combination layer 2 of the part P comprises an upper layer 2a of black color and measuring around ten micrometers.
• This upper layer 2a has been made porous by the HF quenching, and is clearly revealed by the Nital.
• the combination layer is slightly degraded following the HF quenching, but remains present, and retains its structural integrity at least on its lower part 2b.
• Such an upper layer 2a is not observed in FIG. 7.
• the structure of the combination layer has in fact not been modified since there has been no quenching.
• Part P according to the invention therefore indeed has a combination layer 2 providing the part with properties of resistance to wear and friction, and of resistance to corrosion, despite the fact that the HF hardening has been carried out. without protective film.
• FIG. 9 is an assembly juxtaposing a micrograph of a part P according to the invention, and a hardness profile obtained by measurements on this same part. Hardness measurement points are visible on the micrograph and measurement steps corresponding to the different layers have been framed.
• the partially oxidized combination layer 2 and the induction layer 4 are particularly visible.
• Hardness measurements taken just below the suit layer show a hardness of up to 900HV. As you move away from the surface of the part and down towards the core of the part, the hardness decreases in an almost linear fashion, which makes it possible to estimate the thickness of diffusion zone 3 at about 175 ⁇ m, where the depth is. hardness is 775HV.
• the hardness is generally stable at values between 550 and 600HV. These depths are located in the induction treatment zone, which is visually detectable on the micrograph from the crystallography of the part.
• Measurements taken from a depth of 600pm and beyond are located in the base material of the part, i.e. the core of the part, which has not received any treatment.
• the hardnesses recorded are around 250HV.
• a smooth 42CD4 steel ring with ARCOR nitrocarburizing alone hereinafter referred to as "ARCOR ring”
• ARCOR ring A smooth 42CD4 steel ring with ARCOR nitrocarburizing alone, hereinafter referred to as "ARCOR ring”
• ARCOR ring A smooth 42CD4 steel ring with ARCOR nitrocarburizing and HF quenching according to the invention.
• FIG. 10 is a graph illustrating the evolution of the coefficient of friction of these two rings as a function of the number of revolutions performed. On the ordinate is the coefficient of friction m (without unit), and on the abscissa is the number of revolutions Rev (in turns) that the ring undergoes.
• the ARCOR ring alone has a new coefficient of friction m of about 0.15, and that it begins to increase regularly from only 2000 revolutions, until reaching high values, of the order of 0.6 for about 9000 turns.
• Part P according to the invention has, when new, a coefficient of friction slightly lower than that of the ARCOR ring alone, of the order of 0.1, and remains stable up to approximately 11,000 revolutions. It is only from this value that the coefficient of friction begins to increase, reaching a value of 0.6 at approximately 125,000 revolutions, similar to that of the ARCOR ring alone.
• Figures 11 and 12 are photographs respectively of the ARCOR ring alone and of the part P according to the invention, after these tests. It can be seen that the ARCOR ring alone shows marked wear, material having been torn off by seizing. Part P for its part exhibits less pronounced wear.
• FIG. 13 is a close-up view of the micrograph of FIG. 4, centered on the induction layer 4.
• the thickness of the induction layer 4 is represented by the segment [AB]
• An image processing of the figure 13 makes it possible to estimate the proportion of the zones made up of ferrite Fe (a) in the induction layer, that is to say compared to the sum of the zones of ferrite Fe (a) and the zones of martensite Fe (at'). More precisely, by defining lower and upper gray level thresholds, we can estimate the air occupied by the medium gray zone of the martensite phase and thus go back to the ferrite level. It is advisable to use two thresholds and to vary them in order to arrive at this estimate, because although the ferrite appears in clear, the phase interfaces can appear dark and for small ferrites this cannot be negligible. .
• the rate of residual ferrite with respect to the rest of the layer delimited by the segment [AB] is between 1% and 15%, it being understood that this rate tends towards 1% near the combination layer (point A), and tends to 15% near the heart (point B).
• the level of residual ferrite is volume.
• the treatment method according to the invention makes it possible to obtain a level of residual ferrite in the part, between the diffusion zone 3 / combination layer 2 interface and a depth of 500 ⁇ m (segment [AB]) , greater than or equal to 1%, preferably greater than or equal to 5%.
• the treatment method according to the invention makes it possible to obtain a level of residual ferrite in the part, between the diffusion zone 3 / combination layer 2 interface and a depth of 500 ⁇ m (segment [AB]), less than or equal to 50%, preferably less than or equal to 30%, more preferably less than or equal to 20%, and more preferably less than or equal to 15%.
• the level of residual ferrite is between 1% and 20%, preferably between 5% and 15%.
• the manufacturing process can optionally include an impregnation step, in order to improve the corrosion resistance of part P.
• the impregnation takes place after induction hardening.
• Impregnation in itself is a technique well known to those skilled in the art, and a particular method is described, for example, in document EP3237648. Impregnation can be done by dipping or spraying.
• Impregnation protects the part because it helps to delay the onset of corrosion, reduce the corrosion rate and thus increase the life of the part.
• An evaluation of the resistance of the parts to corrosion can be made by tests in a corrosive atmosphere, for example a salt spray.
• Standard EN ISO 9227 “Corrosion tests in artificial atmospheres - Salt spray tests” describes such tests.

Landscapes

• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Materials Engineering (AREA)
• Mechanical Engineering (AREA)
• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Chemical Kinetics & Catalysis (AREA)
• Physics & Mathematics (AREA)
• Thermal Sciences (AREA)
• Crystallography & Structural Chemistry (AREA)
• Heat Treatment Of Articles (AREA)
• Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)

Applications Claiming Priority (2)

Publications (1)

Family

ID=71111478

Family Applications (1)

Country Status (11)

Families Citing this family (1)

Family Cites Families (8)

• 2019
  • 2019-12-24 FR FR1915524A patent/FR3105262B1/fr active Active
• 2020
  • 2020-12-23 AU AU2020411028A patent/AU2020411028A1/en active Pending
  • 2020-12-23 CN CN202080090077.6A patent/CN114846160B/zh active Active
  • 2020-12-23 WO PCT/FR2020/052620 patent/WO2021130460A1/fr active Application Filing
  • 2020-12-23 KR KR1020227021411A patent/KR20220115576A/ko unknown
  • 2020-12-23 US US17/783,544 patent/US20230029324A1/en active Pending
  • 2020-12-23 BR BR112022010610A patent/BR112022010610A2/pt unknown
  • 2020-12-23 CA CA3160425A patent/CA3160425A1/fr active Pending
  • 2020-12-23 MX MX2022007942A patent/MX2022007942A/es unknown
  • 2020-12-23 EP EP20851331.7A patent/EP4045689A1/fr active Pending
• 2022
  • 2022-05-25 ZA ZA2022/05809A patent/ZA202205809B/en unknown

Also Published As

Similar Documents

Legal Events