EP3263726A1 - Matériau à base de fe et son procédé de fabrication - Google Patents

Matériau à base de fe et son procédé de fabrication Download PDF

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Publication number
EP3263726A1
EP3263726A1 EP16176840.3A EP16176840A EP3263726A1 EP 3263726 A1 EP3263726 A1 EP 3263726A1 EP 16176840 A EP16176840 A EP 16176840A EP 3263726 A1 EP3263726 A1 EP 3263726A1
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Prior art keywords
base material
matrix
hard
mass
hard material
Prior art date
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EP16176840.3A
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German (de)
English (en)
Inventor
Horst HILL
André VAN BENNEKOM
Andreas Mohr
Arne RÖTTGER
Werner Theisen
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Ruhr Universitaet Bochum
Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG
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Ruhr Universitaet Bochum
Deutsche Edelstahlwerke GmbH
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Priority to EP16176840.3A priority Critical patent/EP3263726A1/fr
Publication of EP3263726A1 publication Critical patent/EP3263726A1/fr
Withdrawn legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0292—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with more than 5% preformed carbides, nitrides or borides
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B22F3/1035—Liquid phase sintering
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/14—Both compacting and sintering simultaneously
    • B22F3/15—Hot isostatic pressing

Definitions

  • the invention relates to an Fe base material which consists of a steel matrix and of hard particles embedded in the steel matrix.
  • the invention relates to a method for producing such an Fe base material.
  • the Fe base material according to the invention is a so-called "hard composite material" in which the hard particles embedded in the steel matrix should ensure the required hardness and the steel matrix, on the one hand, a secure hold of the hard material particles and, on the other hand, the required toughness of the Fe base material.
  • Fe base material includes iron-based materials, including, in addition to the steels with carbon contents of up to 1% by mass, in particular also in the technical sense, carbon-free materials.
  • powder metallurgy in the form of a metal matrix composite (“MMC”) produced material contains up to 50% by volume (corresponding to up to about 35% by mass) of titanium carbide (TiC ) with a hardness of 2800 - 3500 HV0.05.
  • TiC titanium carbide
  • the Titanium carbide is incorporated in this material into a matrix of steel, the properties of which are adapted to the respective intended use.
  • Ferro-titanitic materials are available, as detailed in the Ferro-Titanit® datasheet collection 08/2003, in which the steel matrix consists of a martensitic, highly resistant steel, a highly corrosion-resistant steel, a hardenable, high tenacity nickel martensitic steel or made of a non-magnetizable, highly corrosion and temper resistant steel.
  • the contents of the respective materials on the particulate TiC hard material grains are typically in the range of 30-35 mass% in practice.
  • Hard composites are preferably used in areas where technical surfaces must be protected against grossly abrasive wear.
  • the structure of hard composites usually consists of a metallic matrix with embedded and finely dispersed hard materials and has in comparison to molten metallurgically urgeformten hard alloys the advantage that material structure against thermodynamic boundary conditions by mixing and compacting any hard metal matrix combinations can be produced.
  • the metal matrix is preferably Fe (white cast iron, tool steels), Ni (NiBSi, NiCrBSi) or Co (Stellite) hard alloys.
  • metallic hard materials or metal-covalently bonded hard materials such as tungsten carbides of the WC or WC-W 2 C type, are usually used because of the metallurgical compatibility and the material properties.
  • the hard composites are usually produced by sintering or build-up welding with the methods presented below, which are known per se to those skilled in the art.
  • solid materials can be produced under pressure and temperature in a known manner or by hard bonding materials on functional surfaces can be applied to functional surfaces by "diffusion welding" (see http://www.ise.rub.de/utz/ête/sintercladding. html.de).
  • a powder, strip or rod-shaped welding filler which is applied to a substrate by suitable fusion welding methods (plasma powder build-up welding, oxy-acetylene welding, metal inert gas welding).
  • the applied by means of build-up welding functional layer protects the substrate against external stress due to wear and / or corrosion.
  • Partly tough Ni base hard alloys with 50% by volume WC or tungsten carbide (“WSC”) have been able to establish themselves as welding consumables.
  • Ni base hard alloys available for hard alloys
  • these materials can be processed together with the additions of hard material at lower temperatures, so that undesirable hard metal-metal matrix interactions, such as the formation of brittle phases, can be avoided.
  • the disadvantage is the cost of these Ni-base / WSC welding consumables.
  • hard material TiC which has a higher hardness compared to W-containing hard materials but a lower fracture toughness.
  • hard composites with the hard material TiC could be produced by sintering and thermal spraying on substrates.
  • tougher grades are used in the field of mining and the treatment of building materials, in particular of materials resulting from road treatment.
  • the structure of these grades also referred to as mining grades, has a lower hard material volume content of 75 to 85 vol .-% with a larger WC carbide size of a few micrometers. Due to a higher co-binder content in the steel matrix in combination with a lower specific carbide surface, a higher wetting surface of the hard materials through the co-binder is present, which promotes the bending strength.
  • Ni base base composites with WSC additions are most commonly processed by build-up welding.
  • the hard material tungsten carbide There is no practical alternative available for the hard material tungsten carbide. This is due to the fact that tungsten carbide as a metal-ceramic material has a good combination of high hardness and high fracture toughness for ceramic materials. There are no commercially available metal-ceramic materials are known which have this combination of properties.
  • Oxide ceramics for example, have a chemically inert effect and do not undergo metallurgical reactions with the metal matrix, so that when they are processed into hard composite materials, they are only frictionally bonded into the metal matrix.
  • covalently bound hard materials in contact with molten metals behave metastable to unstable and lead to the formation of more stable phases.
  • tungsten which is essential for hard materials of the type described here, is available on the market only at high cost and to a limited extent.
  • the object of the invention was to provide an Fe base material that can be produced cost-effectively with secure raw material availability and thereby has optimized service properties.
  • the invention has achieved this object by an Fe base material having at least the features specified in claim 1.
  • the inventive, the above object solving method for producing an Fe base material according to the invention comprises at least the steps specified in claim 7.
  • the invention is based on the recognition that the properties of hard composite materials of the type in question can be purposefully improved by influencing the hard material morphology and the hard material properties.
  • the interdiffusion processes between the metal matrix and the hard material, which begin during the production of the hard composite materials, are used to adjust the hard material properties.
  • the material according to the invention is therefore also a metal-matrix composite ("MMC") in which, according to the invention, optimum bonding of the respectively provided TiC hard materials to the matrix of the material is ensured by adding at least one connecting element.
  • MMC metal-matrix composite
  • the composition of the material forming the matrix of the Fe base material according to the invention is selected such that in the course of the production of the Fe base material it leads to a "alloying" of the hard material provided by the invention in the metallic binder matrix or Metal matrix dissolved alloying elements comes.
  • the alloy of the Fe base material according to the invention is selected such that a sufficient driving force for mass transfer processes occurs at the respective boundary surfaces (steel matrix hard material). In this way, the targeted interdiffusion and the associated changes in the hard material properties achieved.
  • the invention is based on a composition of the Fe base material, which includes the well-known from the prior art members of FerroTitanit materials, but extends this composition by the sake of simplicity so called "attachment elements". These elements have sufficient solubility in the TiC hard material and diffuse during the production of the material from the metal matrix in the TiC hard material bound in the steel matrix.
  • attachment elements such elements which form homologous phases as TiC and thus have a high, partly complete solubility in the kfz lattice of the TiC are used as attachment elements.
  • These elements can be found in the periodic table of elements in the transition elements of the 4th to 6th subgroup. These include Zr, Hf, V, Nb, Ta, Cr, Mo, W, Mn, with "Zr, Hf, Nb, Ta, V, W" being particularly suitable for the purposes according to the invention.
  • Specially tungsten has been included here as a possible attachment element, since it also has a certain solubility in the kfz lattice of the TiC and as far as the other invention selected connecting elements can substitute Ti atoms.
  • the invention thus provides a metal-matrix composite ("MMC") which, with a matrix based on iron and alloyed in accordance with the invention, has optimum conditions for a long and effectively usable service life and also provides optimized performance properties.
  • MMC metal-matrix composite
  • Mo and Cr are preferably not among the attachment elements added according to the invention, because with the diffusion of Mo into the TiC hard material particles, a decrease in the Mo content in the metal matrix surrounding the hard material particles and, concomitantly, a decrease in corrosion resistance would be associated.
  • the selection of the connecting elements according to the invention has succeeded in increasing the corrosion resistance and toughness of the MMC according to the invention.
  • alloying elements have been selected as attachment elements, which have a higher tendency, compared to Mo, to be present in the TiC particles during the production process.
  • tungsten is also suitable for the purposes according to the invention, but has a limited solubility in the TiC and is therefore only effective to a limited extent here.
  • the presence of W in the MMC material according to the invention is preferably completely omitted in the technical sense. W is then present at most in the impurities attributable amounts in the Fe base material according to the invention.
  • the content of the bonding elements added according to the invention as alloying elements to the Fe material of the matrix of an MMC according to the invention is, in principle, 0.5 to 5% by mass per added connecting element.
  • Optimum effects are exhibited by the attachment elements if they are present in the matrix in amounts of at least 1% by mass, the minimum content of the particular attachment element also being 1.5% by mass or 2% by mass can. At levels above the upper limit of 5% by mass of the respective attachment element, no increase in the effect could be observed.
  • Optimal effects were obtained at levels of attachment elements of up to 4% by mass, with contents of not more than 3.5% by mass or not more than 3% by mass regularly resulting in good properties of the MMC-Fe base material according to the invention.
  • the effort associated with the alloying of the connection elements it may therefore be expedient to correspondingly limit the content of the respectively provided connection element.
  • the connecting elements selected according to the invention in combination with one another to the Fe base material according to the invention.
  • the sum of the contents of the added elements is 1-5% by mass, in particular at least 2% by mass or at most 4% by mass.
  • the diffusion is promoted or facilitated.
  • the effects according to the invention of the addition of the attachment elements already set in when only one attachment element is present.
  • Nb and V have been found to be particularly suitable for the purposes of the invention. Extensive investigations have shown that both Nb and V contribute particularly effectively to a significant improvement in the performance of an Fe base material of the type according to the invention. Here, Nb proves to be particularly effective in terms of increasing the wear resistance under the regular operating conditions in practice conditions.
  • Nb alone is provided as the attachment element, it has proved to be favorable if the content of Nb, if present, is less than 5% by mass, in particular not more than 4% by mass, with contents of at least 1% by mass or at least 1.5 mass% have been found to be particularly advantageous. These specifications are especially applicable when the frayed material of the matrix is higher, i. having above 10% by mass lying Cr contents or above 4.5% by mass lying Mo contents. Experiments have shown that the limitation of the Nb content to contents of less than 3% by mass, even at such high Mo or Cr contents, prevents the formation of unfavorable sigma phases.
  • the V content of the Fe base material according to the invention also to at most 5% by mass, in particular at most 4.0% by mass or at most 3.0% by mass
  • contents of at least 1% by mass or 1.5% by mass have proven to be particularly advantageous here.
  • the C content is in the range of the impurities, ie it is not present in the technical sense and therefore ineffective, and its (in mass%) is 12.5-14 , 5, in particular at least 13% or at most 14%, its Mo content 4.5-5.5%, its Co content 8.0-10.0%, in particular at least 8.5% or 9.5%, its Ni content is 3.5-4.5% and its TiC content is 27-33%, in particular at least 29% or at most 31%.
  • the alloy produced according to the invention by the addition of at least one of the attachment elements and the concomitant change in the morphology and size of the TiC particles leads to improved wear resistance.
  • Fine grain (220 mesh) and coarse grain (80 mesh) Al 2 O 3 grains were used as abrasives, it could be shown that according to the invention Anchor elements Nb or V alloyed Fe base material compared to a material that lacked the respective attachment element with otherwise the same composition, in the fine abrasives by a factor of 3.5 and the coarse abrasives showed a factor of 2 improved wear resistance.
  • the powder mixture provided according to the invention can be produced in a conventional manner.
  • the procedures required for this purpose are known and are described, for example, in the brochure " INTRODUCTION TO THE POWDER METALLURGY PROCESSES AND PRODUCTS ", published in the German version by the Powder Metallurgy Association 2010 has been issued and available at the URL www. Pulvermetallurgie.com is available for download, generally described.
  • an explanation of the in the production and processing of hard materials containing metal powders can be found in Foller, M .; Meyer, H .; Lammer, A .: Wear and Corrosion of Ferro-Titanite and Competing Materials.
  • Tools in the next century Proceedings of the 5th International Conference on Tooling, September 29th - October 1st, University of Leoben, Austria, 1999, pp. 1-12 ,
  • the parameters of the sintering can be selected in the compacting step in a manner also known per se so that partial melting of the powder grains occurs.
  • the resulting liquid phase results in practice-oriented process management an optimized binding of the powder grains.
  • the sintering can be carried out in a likewise known manner under pressure.
  • a variant of this sintering process which is particularly suitable for the purposes according to the invention is the so-called hot isostatic pressing, also known by the name "HIP”.
  • the resulting Fe base material block is subjected, if necessary, still a heat treatment in which it is solution-annealed over a period of 1 - 4 hours at a solution annealing temperature of 800 - 1100 ° C.
  • the solution annealing can be carried out under vacuum.
  • the MMC-Fe base material block can also be quenched to obtain a product optimized in mechanical properties. Quenching is preferably carried out in such a way that a purely martensitic structure of the matrix is set up, in which small, technically unavoidable contents of other structural constituents of up to 1% by volume can be present. These other structural constituents may in particular be retained austenite. By creating a purely martensitic structure of the matrix in this sense the required hardness, strength and wear resistance of the MMC material according to the invention safely achieved.
  • the quenching can be done for example by blowing the block of material with respect to the material according to the invention in particular inert gas.
  • the gas stream can be passed at a pressure of 1 - 4.5 bar in a chamber in which the Fe base material block is located.
  • Particularly suitable for the cooling of gaseous nitrogen is particularly suitable.
  • the cooling can be carried out in the furnace chamber in which the annealing treatment has previously taken place.
  • normally openable flaps or the like are provided in heat treatment furnaces used in practice via which, for example by means of fans, the cooling gas, in particular the nitrogen, can be led into the furnace space where it can be circulated and circulated.
  • the cooling gas flow is preferably not directed as a focused nitrogen jet to the refrigerated goods, but passed diffusely into the open chamber. In this way, cooling takes place via the maintained in the furnace chamber and, if necessary, continuously exchanged cooling gas atmosphere.
  • the cooling gas in particular the nitrogen, is preferably used at room temperature. It has been found that, with regard to the goal of cooling, namely the formation of a martensitic microstructure, optimized cooling rates result. At lower cooling gas temperatures, the cooling rates would still be increased somewhat. However, experience shows that this has no appreciable influence on the cooling result, so that the expense associated with the additional cooling of the cooling gas can be avoided
  • Optional solution annealing and optional quenching may be followed by annealing at the end of the heat treatment (optional step c)), where the Fe base material block is heated at 100-550 ° C for a period of 1 - 8 hours is held.
  • the Fe base material block is heated at 100-550 ° C for a period of 1 - 8 hours is held.
  • intermetallic phases are formed which further increase the hardness and strength of the matrix.
  • MMC powders made of a steel matrix forming powder and powdered titanium carbide in an attritor by mechanical alloying have been provided to form a very homogeneous and fine-grained powder.
  • a typical d50 value of the powder was in the range of 10 - 15 ⁇ m. That is, the diameter of 50% of the particles is smaller than 10 - 15 ⁇ m.
  • the mixing was followed by drying and pressing followed by sintering in a vacuum oven in the temperature range of 1200-1500 ° C. over a period of 3 hours at a reduced pressure of about 5 ⁇ 10 -2 mbar.
  • the samples were then solution annealed at 850 ° C for two hours, quenched in oil, and then purged for 6 hours at 480 ° C in air.
  • compositions of the test pieces obtained are shown in Table 1.
  • Nikro 128 is the middle one Hard particle diameter, the mean hard particle size, the volume fraction of hard particles and the number of particles for each sample specified.
  • the Nb-alloyed samples registered a density increase with increasing Nb content due to the higher density of Nb compared to the density of the non-Nb or V-alloyed Nikro128 material. The same has been observed in the V-alloyed samples, since V also has a higher density than the non-Nb or V-alloyed Nikro128 material.
  • microstructure was evaluated metallurgically and the property changes associated with the addition of Nb or V were determined by tribological, mechanical and chemical analyzes.
  • FIGS. 1a-1d The structure of the alloyed with Nb additions Nikro128 materials is in the FIGS. 1a-1d represented by micrographs ( Fig. 1a : Nikro128 + 1Nb; Fig. 1 b: Nikro128 + 2Nb; Fig. 1 c: Nikro128 + 3Nb, Fig. 1d : Nikro128 + 4Nb).
  • Fig. 2 reproduced the microstructure of the material Nikro128 without Nb addition in a similarly prepared microsection.
  • the hard phase size of the TiC inclusions increases and, on the other hand, the free matrix path length between the TiC islands is increased by the breaking up of the reticulated hard materials.
  • the increase in the free matrix path length leads to a significant increase in the bending strength of the Nb-alloyed hard composite materials compared to the starting material Nikro128.
  • both the hardness and the modulus of elasticity of the hard materials can be increased in a targeted manner by alloying in Nb or V, in which case a maximum hardness of approximately 2% by mass V and approximately 2% by mass Nb is achieved becomes. Above these levels, both hardness and modulus drop slightly, with hardness and modulus not falling below the properties of the stoichiometric pure TiC.
  • the modification of the micromechanical properties, the hard material morphology and the chemical composition of the TiC inclusions additionally have a positive influence on the corrosion and wear properties of the Fe base material.
  • FIGS. 3a, 3b attached pictures shows the wear resistance of the tested samples ( Fig. 3a : Nikro 128 + xV; Fig. 3b : Nikro128 + xNb), testing for claw wear.
  • the tests were done in the manner already described as pen paper Wear test performed.
  • FIGS. 3a, 3b show that, compared to the coarse abrasives, the addition of V only causes a slight increase in the wear resistance compared to the Nikro128 without Nb or V.
  • the wear resistance increases with increasing Nb content due to an increase in hardness, volume content and diameter of the hard material TiC with increasing Nb content.
  • the thus prepared samples were installed as a working electrode in a test stand.
  • the counterelectrode consisted of a platinum plate, while the reference electrode was made of mercuric chloride and was spatially separated but electrically connected via a salt bridge in an external vessel. This separation was made to counteract contamination of the electrode and thus a falsification of the measurement results. Either 0.5 mol H2SO4 (5%) or 0.6 mol NaCl (3%) was used. All electrodes were connected to a potentiostat, which took over the regulation of the voltage and the measurement of the current.
  • the sulfuric acid Prior to measurement and after incorporation of the sample into the test stand, the sulfuric acid was purged with nitrogen (2 L / min) for 30 minutes to purge contained oxygen for comparability of results. Subsequently, the sample became cathodic for 60 s -1744 mV cathodized. This serves to remove impurities on the surface and at least a partial dissolution of the natural oxide layer. In the subsequent measurement of the resting potential for 30 min, the passive layer formed with the oxygen in the electrolyte and thus always under comparable conditions new.
  • the hole corrosion behavior was determined in 0.6 molar NaCl solution. Since in most cases the actual pitting potential Upit, ie the potential indicating the onset of pitting corrosion at the beginning of the steep rise of the potential curve, could not be determined correctly, based on the currently valid standards ASTM G-150-99 and DIN-50905- 2 introduced the breakthrough potential as a benchmark. This value was read at the location of the curve, from which the current density is constant> 100 ⁇ A / cm 2 .
  • Fig. 4 the measured curves determined for the V-containing samples and the sample alloyed neither with V nor Nb are shown for the determination of the breakdown potential (at 100 ⁇ A / cm 2 ). It can be seen that as the V content increases, the breakdown potential is shifted in the direction of higher potentials and therefore the corrosion resistance (in this case compared with NaCl) increases.
  • the interdiffusion process between hard materials, such as TiC, and the metal matrix occurring during the alloying of a connecting element, in particular during the alloying of Nb and V can be used selectively during the compaction of materials containing hard materials.
  • the metal matrix is targeted with sufficient levels Enriched alloying elements that interact chemically during the material compaction with the hard materials and possibly cause the formation of new phases.
  • the alloying-in of hard materials by alloying elements according to the invention from the metal matrix during the production of the Fe base material according to the invention thus makes it possible to influence the hard material properties in a targeted manner.
  • the result is improved material properties compared to conventionally produced hard composite materials.
  • the invention focuses on the use of TiC hard materials that are available in sufficient quantities and sustainable.
  • the inventive MMC-Fe base material can be produced in a particularly cost-effective manner if the TiC contained in it is at least partially obtained by recycling Ti-containing Fe base materials.
  • a method of recycling such materials is in the EP 2 678 455 B1 described.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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EP16176840.3A 2016-06-29 2016-06-29 Matériau à base de fe et son procédé de fabrication Withdrawn EP3263726A1 (fr)

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CN109022994A (zh) * 2018-09-12 2018-12-18 天津百世康科技发展有限公司 耐磨耐腐蚀的碳化物钢复合材料
CN113732285A (zh) * 2021-11-05 2021-12-03 西安赛隆金属材料有限责任公司 一种铁镍钴基粉末合金及提高其延伸率的方法

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109022994A (zh) * 2018-09-12 2018-12-18 天津百世康科技发展有限公司 耐磨耐腐蚀的碳化物钢复合材料
CN113732285A (zh) * 2021-11-05 2021-12-03 西安赛隆金属材料有限责任公司 一种铁镍钴基粉末合金及提高其延伸率的方法

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