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WO2022218469A1 - Procédé de production d'un composant de transmission harmonique, composant de transmission et transmission harmonique - Google Patents

Procédé de production d'un composant de transmission harmonique, composant de transmission et transmission harmonique Download PDF

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Publication number
WO2022218469A1
WO2022218469A1 PCT/DE2022/100258 DE2022100258W WO2022218469A1 WO 2022218469 A1 WO2022218469 A1 WO 2022218469A1 DE 2022100258 W DE2022100258 W DE 2022100258W WO 2022218469 A1 WO2022218469 A1 WO 2022218469A1
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WO
WIPO (PCT)
Prior art keywords
weight
blank
harmonic drive
component
drive component
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/DE2022/100258
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German (de)
English (en)
Inventor
Markus Dinkel
Gregor HULLIN
Jochen Damerau
Stefan Birkner
Igor MYS
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.)
Schaeffler Technologies AG and Co KG
Original Assignee
Schaeffler Technologies AG and Co KG
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
Priority claimed from DE102022108012.9A external-priority patent/DE102022108012A1/de
Application filed by Schaeffler Technologies AG and Co KG filed Critical Schaeffler Technologies AG and Co KG
Priority to KR1020237034846A priority Critical patent/KR20230158027A/ko
Priority to JP2023562587A priority patent/JP2024514142A/ja
Priority to CN202280027870.0A priority patent/CN117120637B/zh
Publication of WO2022218469A1 publication Critical patent/WO2022218469A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • 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
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • 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
    • C21D9/30—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for crankshafts; for camshafts
    • 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
    • C21D9/40—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rings; for bearing races
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/40—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
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16H—GEARING
    • F16H55/00—Elements with teeth or friction surfaces for conveying motion; Worms, pulleys or sheaves for gearing mechanisms
    • F16H55/02—Toothed members; Worms
    • F16H55/06—Use of materials; Use of treatments of toothed members or worms to affect their intrinsic material properties
    • 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
    • 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
    • C21D2261/00—Machining or cutting being involved
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16H—GEARING
    • F16H55/00—Elements with teeth or friction surfaces for conveying motion; Worms, pulleys or sheaves for gearing mechanisms
    • F16H55/02—Toothed members; Worms
    • F16H55/17—Toothed wheels
    • F16H2055/176—Ring gears with inner teeth
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16H—GEARING
    • F16H49/00—Other gearings
    • F16H49/001—Wave gearings, e.g. harmonic drive transmissions

Definitions

  • the invention relates to a method for producing a harmonic drive component. Furthermore, the invention relates to a strain wave gear component and a strain wave gear.
  • DE 102016219076 A1 shows a strain wave gear with a flexible, externally toothed gear component and with a further internally toothed gear component that meshes with it.
  • the further transmission component has a cylindrical, internally toothed, rigid sleeve section and a disk-shaped, elastically flexible bottom section connected to this.
  • a collar sleeve of such a strain wave gear is made, for example, from heat-treated steel in the strength range of 1100-1300 MPa.
  • a ring gear is made, for example, from ausferritic cast iron with a strength of 900 to 1200 MPa.
  • the manufacture of both the ausferritic cast and the steel component generally consists of thorough heat treatment, hardening (martensitic or bainitic) and subsequent tempering (quenching and tempering) to the desired target strength.
  • the component geometries of the heat-treated component are then formed using conventional production technologies, ie turning, drilling, milling, in particular hobbing, skiving or slotting or broaching the gearing.
  • Components manufactured in this way achieve strengths of up to 400 HV.
  • JP 2595609 B2 discloses a free-cutting steel that can be produced by means of carburizing hardening.
  • the steel contains, by weight, one or more kinds of 0.10 to 0.30% carbon (C), 1.0% or less silicon (Si), 3.0% or less manganese (Mn), or less 8.0% chromium (Cr), 5.0% or less nickel (Ni), 6.0% or less molybdenum (Mo), and 2.0% or less aluminum (AI).
  • Aluminum reduces the amount of oxygen in the steel and at the same time improves its ability to be nitrided.
  • JP 2 595609 B2 sees it as advantageous to use 0.005% AI. The higher the Al content, the greater the impact on the toughness of the material.
  • the steel also contains, by weight, 0.004 to 0.020% boron (B), 0.005 to 0.050% nitrogen (N) and less than or equal to 0.0015% oxygen (O).
  • a ratio between nitrogen and boron is 0.5 to 4.0 N/B.
  • the total amount of elements with high nitride formation degree of elution such as titanium (Ti) and zirconium (Zr) is less than or equal to 0.01%.
  • the rest consists of iron (Fe).
  • boron and nitrogen form boron nitride inclusions.
  • JP 2805845 B2 discloses a steel containing, by weight, 0.10 to 0.30% by weight of carbon (C), one or more types of 3.0% or less manganese (Mn), 8.0% or less Chromium (Cr), 5.0% or less Nickel (Ni), 6.0% or less Molybdenum (Mo) and 2.0% or less Aluminum (Al), and 0.004 to 0.020% Boron (B) and 0.005 to 0.050% nitrogen (N), with a ratio between nitrogen and boron of 0.5 to 0.4 N/B.
  • the steel also consists of less than or equal to 0.0015% oxygen (O), less than or equal to 0.10% silicon (Si) and less than or equal to 0.015% phosphorus (P).
  • the total amount of high nitriding elements such as titanium (Ti) and zirconium (Zr) is 0.01% or less.
  • the rest consists of iron (Fe).
  • the object of the present invention is to further develop a method for preparing a strain wave gear component, a strain wave gear component and a strain wave gear.
  • a method according to the invention for manufacturing a strain wave gear component, in which the strain wave gear component is formed from a precipitation-hardening steel, comprises the steps:
  • solution annealing of the blank, where the solution annealing is carried out either by heating the blank to a solution annealing temperature between 950 and 1050 °C or during a forging operation at a temperature between 1000 and 1200 °C until precipitation hardening components of the composition are in solution;
  • the blank is formed from a precipitation hardening steel and may be in the form of rolled bar stock before being heat treated.
  • the blank can be made by cutting or forging.
  • the blank can be formed into a ring shape by forging or the like.
  • a precipitation hardening steel is a steel whose hardness can be adjusted by precipitation hardening depending on the process parameters and the alloy composition.
  • the blank can be provided for the heat treatment in any desired machining state, for example in a substantially unmachined state, with all or at least a large part of the mechanical machining for producing a geometry of the corrugated gear component component that is at least close to the net shape after the solution annealing and cooling of the blank takes place at room temperature.
  • the blank can also already be formed essentially close to the net shape, with the blank only being subjected to final machining after solution annealing and cooling of the blank, for example to remove distortion and machine the strain wave gear component to its final dimensions.
  • the alloy composition of the blank or the corrugated transmission component made from it has 0.01 to 0.35% by weight carbon (C), 0 to 0.15% by weight silicon (Si), 0 to 0.4% by weight -% manganese (Mn), 4.5 to 5.5 wt% chromium (Cr), 4.5 to 6.5 wt% nickel (Ni), 0.5 to 1 wt% molybdenum ( Mo), 0 to 0.6% by weight vanadium (V), 2 to 2.5% by weight aluminum (AI), 0 to 0.008% by weight sulfur (S), 0 to 0.02% by weight -% Phosphorus (P), 0 to 0.025% by weight Titanium (Ti), 0.005 to 0.015% by weight Nitrogen (N), 0 to 0.007% by weight Oxygen (O), 0 to 0.0035% by weight % potassium (K), 0 to 0.015% by weight magnesium (Mg) and the remainder iron (Fe) and unavoidable trace elements.
  • the trace elements are impurities
  • the material has a high alloy content of elements that increase hardenability, such as chromium and nickel.
  • elements that increase hardenability such as chromium and nickel.
  • solution annealing During solution annealing, precipitations present in the structure of the blank, in particular carbide precipitations and other phases in the mixed crystal, are dissolved, with the structure being prevented from reprecipitating by cooling the blank to room temperature.
  • the blank is cooled to room temperature at such a cooling rate that an essentially martensitic structure is present.
  • solution annealing serves to recrystallize cold-worked microstructure areas and thus reduce strain hardening. For example, after rapid heating, the blank is held in the range from 950 to 1050°C, depending on the component dimensions.
  • the solution annealing takes place in particular until the precipitation-hardening components of the composition are in solution. When this point in time occurs as a function of the alloy composition can be determined in advance using well-known simulation methods.
  • a temperature selected for the solution annealing is preferably chosen so high that no unwanted, coarse particles in the structure ge remain, which are disadvantageous for the mechanical properties of the material.
  • the temperature for the solution annealing is chosen so low that the eutectic temperature of the alloy is not exceeded in order to prevent segregation.
  • the preferred solution treatment time is not less than 30 minutes and not more than 90 minutes. Ideally, the precipitation-hardening components are completely dissolved in the matrix after approx. 45 minutes.
  • the condition of the blank in which the precipitation-hardening components of the composition are in solution can be achieved by forging the blank, advantageously at a temperature of between 1000 and 1200°C. During forging, the precipitations or phases mentioned go into solution, so that the blank is in the solution-annealed condition after forging and cooling to room temperature.
  • the cooling of the blank to room temperature which immediately follows the solution annealing, can in principle be designed as desired.
  • the blank has an essentially martensitic structure after cooling.
  • the hardenability of the material after solution annealing or after forging is so high that the cooling rate has no significant influence on the fact that an essentially martensitic basic structure is present after cooling, whereby almost identical hardness is always achieved even with short, moderate or long becomes.
  • the blank with the steel composition mentioned is an air-hardening steel which can also be cooled in air in order to achieve the desired material properties, in particular the required hardness and/or strength. The steel therefore has no pronounced sensitivity to the cooling curve during cooling.
  • martensitic hardening can be carried out after solution annealing, with the blank being quenched to room temperature in a suitable medium, starting from the solution annealing temperature.
  • room temperature means an ambient temperature between 10 and 40.degree. C., preferably between 15 and 25.degree.
  • the blank can be mechanically processed in such a way that the geometry of the harmonic drive component is essentially close to the final contour.
  • the blank is machined to its final dimensions using suitable mechanical machining steps.
  • Mechanical processing is to be understood, for example, as meaning cutting manufacturing or machining processes such as milling, turning, drilling, sawing and floning.
  • a gearing be it internal or external gearing
  • the blank can therefore be machined to the final dimensions of the harmonic drive component in the soft, i.e. solution-annealed, state using conventional technologies.
  • precipitation hardening also known as hardening, which essentially serves to increase the strength, in particular the yield point, of the harmonic drive component. This results in the separation of finely divided, intermetallic phases that make it difficult for dislocation movements within the crystal lattice to occur as a result of deformations caused by internal stresses or plastic deformation.
  • the precipitation hardening is advantageously carried out at a temperature between 450 and 650°C for at least 30 minutes and at most 10 hours. Short times and high temperatures are particularly useful in order to allow the hardness to increase quickly.
  • the advantage of precipitation hardening in the context of the method proposed here consists essentially in the fact that the harmonic drive component exhibits no or only minimal changes in shape or volume in the course of precipitation hardening.
  • the final component strength of the corrugated gear component is set by precipitation hardening.
  • Another advantage of the process is that there is no rapid cooling compared to conventional precipitation-hardened steels after forging or solution heat treatment, which significantly reduces distortion in the blank.
  • the blank is preferably solution annealed and then cooled until it has a hardness of between 350 and 500 HV5.
  • the hardness is essentially based on the hardening potential due to the carbon content, which is less than 0.2% by weight to almost 0.3% by weight, so that the hardness range between 350 and 500 HV5 is achieved. Hardness is measured after cooling at room temperature.
  • a hardness of 350 HV (Vickers hardness) corresponds to a Rockwell hardness of about 35.5 HRC and a Vickers hardness of 500 HV corresponds to a Rockwell hardness of about 49.1 HRC.
  • the blank is solution annealed until it has a Rockwell hardness of between 35.5 and 49.1 HRC.
  • the hardness values are determined using the Vickers hardness test, which is used to test homogeneous materials and is also suitable for testing the hardness of thin-walled or surface-hardened workpieces and edge zones. This test procedure is regulated in the standard according to DIN EN ISO 6507-1:2018 to -4:2018. A suitable test force for determining the hardness is 5 kiloponds. However, other test forces can also be used.
  • the hardness of the strain wave gear component is only increased by approx. 150 to 250 HV with the additional tempering treatment by means of precipitation hardening.
  • the strain wave gear component has a hardness of between 550 and 750 HV5.
  • a Vickers hardness of 550 HV corresponds to a Rockwell hardness of about 52.3 HRC
  • a Vickers hardness of 750 HV corresponds to a Rockwell hardness of about 62.2 HRC. Consequently, the strain wave gear component is precipitation hardened until it has a hardness between 52.3 HRC and 62.2 HRC.
  • the harmonic drive component preferably has a strength of at least 1600 MPa. This can be adjusted in particular by adjusting the carbon content in the composition. For example, with a carbon content of approx. 0.05% by weight, the maximum strength is approx. 1650 MPa, with a carbon content of approx approx. 1850 MPa and with a carbon content of approx. 0.28% by weight, a strength of more than 1900 MPa can be achieved.
  • a harmonic drive component has a precipitation-hardening steel with the composition 0.01 to 0.35% by weight carbon, at most 0.15% by weight silicon, at most 0.4% by weight manganese, 4.5 to 5.5 By weight chromium, 4.5 to 6.5% by weight nickel, 0.5 to 1% by weight molybdenum, at most 0.6% by weight vanadium, 2 to 2.5% by weight aluminum 0.008% by weight sulfur maximum, 0.02% by weight maximum phosphorus, 0.025% by weight maximum titanium, 0.005 to 0.015% by weight nitrogen, 0.007% maximum oxygen by weight, 0.0035% maximum by weight -% potassium, at most 0.015% by weight magnesium and the remainder iron with unavoidable trace elements.
  • the strain wave gear component preferably has carbides of the M6C and/or MC type. These carbides form during precipitation hardening.
  • An example of type M6C carbides is a chromium carbide of the form Cr6C, an example of type MC is vanadium carbide of the form VC.
  • the harmonic drive component preferably has nickel aluminide precipitates with a maximum size of 100 nm. Such precipitations have the composition NiAl and show good material properties for the harmonic drive component.
  • the strength of the harmonic drive component can be increased by approx. 200 to 250 FIV compared to the solution-annealed condition using the precipitations mentioned.
  • a harmonic drive according to the invention comprises a harmonic drive component according to a second aspect of the invention.
  • the harmonic drive comprises, for example, a flexible collar sleeve with external teeth that can be deformed locally and radially around the circumference by a wave generator with a non-circular outer peripheral surface, and a rigid floating wheel with internal teeth, the external teeth of the collar sleeve being at least partially in contact with the internal teeth to transmit a torque to at least one toothed meshing area of the flea wheel is in tooth mesh.
  • the Wellge transmission component can be the fleet wheel of the harmonic drive.
  • the strain wave gear component can also be the collar sleeve of the strain wave gear.
  • Figure 1 shows a schematic sectional view of a corrugated gear component according to the invention according to a first embodiment, the corrugated gear component being designed as a floating wheel,
  • FIG. 2 shows a schematic sectional representation of the corrugated transmission component according to the invention according to a second embodiment, the corrugated transmission component being designed as a collar sleeve, and
  • FIG. 3 shows a schematic block diagram of a method according to the invention for fixing the harmonic drive component according to FIG. 1 or FIG.
  • the figures show a method according to the invention for fixing a harmonic drive component 1, which is shown as an example according to FIG. 1 as a floating wheel 2 of a harmonic drive (not shown here) and as a collar sleeve 3 of the harmonic drive according to FIG. 2, according to a block diagram.
  • a harmonic drive component 1 which is shown as an example according to FIG. 1 as a floating wheel 2 of a harmonic drive (not shown here) and as a collar sleeve 3 of the harmonic drive according to FIG. 2, according to a block diagram.
  • the block diagram for the description of the preparation method is shown in FIG.
  • the floating wheel 2 and/or the collar sleeve 3 are consequently intended to be used in the harmonic drive.
  • a blank (not shown here) is produced, the blank being formed from a precipitation-hardening steel as rolled bar steel which is brought into a ring shape by forging.
  • the composition of the blank is 0.01 to 0.35% by weight carbon, at most 0.15% by weight silicon, at most 0.4% by weight manganese, 4.5 to 5.5% by weight chromium , 4.5 up to 6.5% by weight nickel, 0.5 to 1% by weight molybdenum, not more than 0.6% by weight vanadium, 2 to 2.5% by weight aluminum, not more than 0.008% by weight sulfur, 0.02% by weight maximum phosphorus, 0.025% by weight maximum titanium, 0.005 to 0.015% by weight nitrogen, 0.007% by weight maximum oxygen, 0.0035% maximum potassium, 0.015% maximum by weight % magnesium and the remainder iron with unavoidable trace elements.
  • the provided blank is solution annealed.
  • the solution heat treatment can be done through two alternative steps.
  • solution annealing can be carried out as a separate heat treatment step, with the blank being heated to a solution annealing temperature of between 950 and 1050 °C and heat-treated until precipitation-hardening components of the composition of the blank are in solution.
  • Such components are, in particular, carbide precipitations and other phases of the mixed crystal.
  • the blank can be subjected to a forging process at a temperature between 1000 and 1200 °C during its production from the rolled bar steel, with the temperature being maintained until the precipitation-hardening components of the composition of the blank are in solution.
  • the blank has a hardness of between 350 and 500 HV5.
  • a third method step 13 the blank is cooled down to room temperature.
  • the cooling takes place in air, but it can also take place in a fluid such as water, oil or gas.
  • a fourth method step 14 the cooling is followed by the mechanical processing of the blank, so that the harmonic drive component 1 is formed from the blank.
  • an internal toothing 4 can be produced on the inner circumference of the ring gear 2 by machining.
  • external teeth 5 can be produced on the outer circumference of the collar sleeve 3 by machining.
  • a geometry of the harmonic drive component 1 that is essentially close to the final contour is produced by means of the mechanical processing of the blank.
  • the strain wave gear component 1 is precipitation hardened in a fifth method step 15 at a temperature of 450 to 650° C. for at least 30 minutes and at most 10 hours.
  • chromium carbides of the Cr6C type and vanadium carbides (VC) are formed in the structure of harmonic drive component 1.
  • nickel aluminide nickel aluminide
  • Precipitations with a size of up to 100 nm Precipitations with a size of up to 100 nm.
  • the precipitations or carbides increase the hardness within the structure by 200 to 250 HV, so that after precipitation hardening the harmonic drive component 1 has a hardness of between 550 and 750 HV5 and a strength of at least 1600 MPa .
  • strain wave gear component 1 comprising a precipitation-hardening steel with the composition 0.01 to 0.35% by weight carbon, at most 0.15% by weight silicon, at most 0.4% by weight Manganese, 4.5 to 5.5% by weight chromium, 4.5 to 6.5% by weight nickel, 0.5 to 1% by weight molybdenum, not more than 0.6% by weight vanadium, 2 up to 2.5% by weight aluminum, not more than 0.008% by weight sulfur, not more than 0.02% by weight phosphorus, not more than 0.025% by weight titanium, 0.005 to 0.015% by weight nitrogen, not more than 0.007% by weight % oxygen, at most 0.0035% by weight potassium, at most 0.015% by weight magnesium and the remainder iron with unavoidable trace elements such as copper, antimony, tin, arsenic or the like.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • General Engineering & Computer Science (AREA)
  • Electromagnetism (AREA)
  • Heat Treatment Of Articles (AREA)
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Abstract

L'invention concerne un procédé de production d'un composant de transmission harmonique (1) constitué d'un acier à durcissement par précipitation. Le procédé comprend les étapes consistant à : - fournir une ébauche qui a la composition de 0,01 à 0,35 % en poids de carbone, au maximum 0,15 % en poids de silicium, au maximum 0,4 % en poids de manganèse, 4,5 à 5,5 % en poids de chrome, 4,5 à 6,5 % en poids de nickel, 0,5 à 1 % en poids de molybdène, au maximum 0,6 % en poids de vanadium, 2 à 2,5 % en poids d'aluminium, au maximum 0,008 % en poids de soufre, au maximum 0,02 % en poids de phosphore, au maximum 0,025 % en poids de titane, 0,005 à 0,015 % en poids d'azote, au maximum 0,007 % en poids d'oxygène, au maximum 0,0035 % en poids de potassium, au maximum 0,015 % en poids de magnésium, et du fer avec des éléments traces inévitables en tant que reste, - recuire en solution l'ébauche, le procédé de recuit en solution étant réalisé soit par chauffage de l'ébauche à une température de recuit en solution comprise entre 950 et 1 050 °C ou pendant un procédé de forgeage à une température comprise entre 1 000 et 1 200 °C jusqu'à ce que des composants de durcissement par précipitation de la composition soient présents dans la solution ; - refroidir l'ébauche à température ambiante ; - usiner mécaniquement l'ébauche pour former le composant de transmission harmonique (1) ; et - durcir par précipitation le composant de transmission harmonique (1) à une température de 450 à 650 °C pendant au moins 30 minutes et au maximum 10 heures. L'invention concerne en outre un composant de transmission harmonique (1) et une transmission harmonique (2).
PCT/DE2022/100258 2021-04-12 2022-04-06 Procédé de production d'un composant de transmission harmonique, composant de transmission et transmission harmonique Ceased WO2022218469A1 (fr)

Priority Applications (3)

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KR1020237034846A KR20230158027A (ko) 2021-04-12 2022-04-06 파동 기어 부품의 제조 방법, 파동 기어 부품 및 파동 기어
JP2023562587A JP2024514142A (ja) 2021-04-12 2022-04-06 減速ギアボックス構成部品を製造するための方法、減速ギアボックス構成部品および減速ギアボックス
CN202280027870.0A CN117120637B (zh) 2021-04-12 2022-04-06 用于制造谐波传动装置构件的方法，谐波传动装置构件和谐波传动装置

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DE102021108990 2021-04-12
DE102021108990.5 2021-04-12
DE102022108012.9A DE102022108012A1 (de) 2021-04-12 2022-04-04 Verfahren zur Herstellung eines Wellgetriebebauteils, Wellgetriebebauteil und Wellgetriebe
DE102022108012.9 2022-04-04

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JP2595609B2 (ja) 1988-01-26 1997-04-02 大同特殊鋼株式会社 浸炭焼入れ用快削鋼
JP2805845B2 (ja) 1989-06-07 1998-09-30 大同特殊鋼株式会社 浸炭焼入れ用快削鋼
EP1514948A1 (fr) * 2002-06-20 2005-03-16 Honda Giken Kogyo Kabushiki Kaisha Bande d'acier comprenant de l'acier martensitique et procede de fabrication d'une courroie pour transmission a changement de vitesses continu utilisant une telle bande d'acier
CN106636927A (zh) * 2016-10-13 2017-05-10 南京创贝高速传动机械有限公司 一种高速齿轮箱用冷却水泵的生产工艺
DE102016219076A1 (de) 2016-09-30 2017-08-17 Schaeffler Technologies AG & Co. KG Wellgetriebe

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* Cited by examiner, † Cited by third party
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US3619179A (en) * 1969-04-22 1971-11-09 Allegheny Ludlum Steel Age-hardening martensitic steels
JP2595609B2 (ja) 1988-01-26 1997-04-02 大同特殊鋼株式会社 浸炭焼入れ用快削鋼
JP2805845B2 (ja) 1989-06-07 1998-09-30 大同特殊鋼株式会社 浸炭焼入れ用快削鋼
EP1514948A1 (fr) * 2002-06-20 2005-03-16 Honda Giken Kogyo Kabushiki Kaisha Bande d'acier comprenant de l'acier martensitique et procede de fabrication d'une courroie pour transmission a changement de vitesses continu utilisant une telle bande d'acier
DE102016219076A1 (de) 2016-09-30 2017-08-17 Schaeffler Technologies AG & Co. KG Wellgetriebe
CN106636927A (zh) * 2016-10-13 2017-05-10 南京创贝高速传动机械有限公司 一种高速齿轮箱用冷却水泵的生产工艺

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CN117120637B (zh) 2025-12-09

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