EP3808864B1 - Premix alloy powders for diamond tools - Google Patents

Premix alloy powders for diamond tools Download PDF

Info

Publication number
EP3808864B1
EP3808864B1 EP19203219.1A EP19203219A EP3808864B1 EP 3808864 B1 EP3808864 B1 EP 3808864B1 EP 19203219 A EP19203219 A EP 19203219A EP 3808864 B1 EP3808864 B1 EP 3808864B1
Authority
EP
European Patent Office
Prior art keywords
composition
powder
diamond
mix
alloy
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.)
Active
Application number
EP19203219.1A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP3808864A1 (en
Inventor
Matteo Zanon
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.)
Ecka Granules Germany GmbH
Original Assignee
Ecka Granules Germany GmbH
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
Application filed by Ecka Granules Germany GmbH filed Critical Ecka Granules Germany GmbH
Priority to EP19203219.1A priority Critical patent/EP3808864B1/en
Priority to ES19203219T priority patent/ES2919199T3/es
Publication of EP3808864A1 publication Critical patent/EP3808864A1/en
Application granted granted Critical
Publication of EP3808864B1 publication Critical patent/EP3808864B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/05—Mixtures of metal powder with non-metallic powder
    • 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%
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C22C38/56—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.7% by weight of carbon
    • 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
    • B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
    • B22F2005/001—Cutting tools, earth boring or grinding tool other than table ware
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents

Definitions

  • the cutting elements are composite materials where diamonds are embedded into a metallic matrix, the so-called “bond". Its role is twofold: to hold the diamond as long as possible, and to wear at a rate compatible with the material being cut.
  • Metal powder is mixed with diamonds (typically 5-10 vol-%), granulated and then cold pressed. The composite is then consolidated close to full density via hot pressing (HP) or free sintering (FS) processes.
  • Matrix formulations have historically been based on cobalt, thanks to its excellent diamond retention, ease of processing by hot pressing and adjustable wear rate (by adding bronze / tungsten carbide).
  • chemically precipitated alloys were developed, based on Fe-Cu-Co system, as a response to instability in Co price and supply ( J. Konstanty, Powder Metallurgy 2013, 56(3), pp. 184-188 ).
  • Such products have gained a significant market share in Europe.
  • Other powder producers offer chemical, mechanically alloyed or also premixed products, based on the Fe-Cu system.
  • Co-free powders already exist since several years, but their performance as compared to Co-containing alternatives is inferior, and thus it was not possible to displace the Co-based alternatives.
  • Premixed powders on the one hand are intrinsically cheaper and can preserve the high compressibility of their constituents.
  • their performance is generally inferior to hydrometallurgical and mechanically alloyed products, mainly due to coarser grain size of their constituents and lack of stored mechanical energy.
  • An example is disclosed in EP-A-2 082 072 directly comparing chemically equivalent hydrometallurgical and premix powders. After 1 h at 950°C, the Fe-Co-Cu-P premix reaches only 89,1% density, while the hydrometallurgical goes up to 97,2%.
  • On the Asian market such products are reported to be gaining ground thanks to their attractive cost (see, e.g., J. Borowiecka-Jamrozek et al., Arch. Metall.
  • the present invention addresses all the requirements herein described, fulfilling them via the introduction of an alloy system not considered in the present field before, namely FeCrBC, and further by choosing and balancing other base constituents. In this way the present invention has been achieved.
  • the present invention provides a powder composition comprising, based on the entire composition, ⁇ 50 wt. and preferably ⁇ 60 wt.-% of the composition of any of claims 1-6, and at least one other material suitable for preparing a matrix (bond) for diamonds in a diamond cutting tool.
  • the present invention provides a process for producing a composite material comprising the steps of
  • the present invention provides a composite material made of diamond and a composition of the present invention, and a diamond tool comprising this composite material.
  • the present invention provides the use of a powder of a XCrBC-alloy powder, wherein X is Fe, Co or Fe and Co, as a diamond binding and/or reinforcing agent.
  • the present invention provides a composition which is a powder composition comprising a mixed powder of the formula (1) Fe a Co b Cu c Sn d Ni e B f Cr g C h (1)
  • Said mixture may then be diluted with other typical materials known to those skilled in the art, such as but not limited to tungsten powder, tungsten carbide (WC), CuAg brazing alloys, bronze powders, Ni-based Ni-Cr-Si-B alloys, NiP, FeP, etc. in order to alter its wear resistance or to confer special properties such as "self-brazing" behavior.
  • a powder composition of the invention comprises, based on the entire composition, ⁇ 50 wt. and preferably ⁇ 60 wt.-% of the composition of the above formula (1) together with at least one other material suitable for preparing a matrix (bond) for diamonds in a diamond cutting tool.
  • premix route in comparison to pre-alloyed products, being the single unalloyed or low-alloyed powders relatively soft and coarse, it guarantees a good compressibility of the green parts. This results in a relatively low shrinkage rate after free sintering, because they start from a density closer to the final one.
  • the final density for most applications needs to be at least around 96-97 % relative to theoretical full density.
  • the inventive mix has Fe and Cu as main constituents. Given their low mutual solubility, they form two distinct phases in the final microstructure, one Fe-rich and the other one Curich.
  • Fe has been used since decades as a lower cost, lower performance substitute for cobalt; it provides the primary diamond bonding, both mechanical as well as metallurgical, being carbon (C), the essential constituent of diamond, highly soluble into Fe.
  • C carbon
  • Fe could be at least partially replaced by cobalt, without contradicting its spirit; in one preferred embodiment however, it is essentially Co-free.
  • iron (Fe) is present in the composition of formula (1) in an amount corresponding to a value of a of 0-85.0, preferably 20.0-80.0, more preferably 30.0-75.0, even more preferably 40.0-70.0, and most preferably 55.0-65.0.
  • the total content of Fe and Co in the powder of formula (1) is 40.0-85.0, preferably 45.0-80.0, more preferably 50.0-75.0, even more preferably 52.0-70.0, and yet more preferably 55.0-65.0.
  • the ratio of Fe and Co in the powder of formula (1) is 0-90.0, preferably 0-40.0, more preferably 0-20.0, and even more preferably 0-10.0.
  • Iron can be introduced under the form of water atomized Fe powder, electrolytic Fe powder, Fe powder made from Fe carbonyl, "sponge" iron made by e.g. direct ore reduction (Höganäs process) or any other market-available powder, in a single form or a combination thereof.
  • PS 95 XX ⁇ m
  • the PS 95 value indicates that about ⁇ 95 wt.-% of the powder particles have a size of less than XX ⁇ m.
  • Cu copper
  • the solubility of carbon into copper (Cu) is negligible.
  • the primary role of Cu in the present powders is to increase the sintering activity of the matrix, by rendering possible its sintering under 1,000°C.
  • Copper is introduced under the form of water atomized, air atomized, gas atomized, electrolytic, oxide-reduced or any other market-available powder in a single form or a combination thereof.
  • Cu is present in the composition of formula (1) in an amount corresponding to a value of c of 10.0-50.0, preferably 15.0-45.0, more preferably 20.0-40.0, and even more preferably 25.0-35.0.
  • Tin (Sn) is added both to reinforce copper phase as well as to lower sintering temperature, given its strong effect on melting point of bronze (Cu-Sn) alloy.
  • Total content of bronze constituents ( c + d ) determines the sintering reactivity of the matrix; if too low it will undermine its densification, if too high will make the bond too weak and soft.
  • the content of Sn in the present composition is 0.1-17.5, preferably 0.5-15.0, more preferably 1.0-10.0, and yet more preferably 1.5-7.0.
  • the proportion of Sn in the bronze phase in other words the ratio d /( c + d ) , can be adjusted and optimized according to sintering temperature. A too low Sn content will however be ineffective, a too high content will generate an excess of brittle delta phase.
  • the total content of Cu and Sn in the powder of formula (1) is 10.1-55.0, preferably 15-50.0, more preferably 25-45, and even more preferably 30-40.
  • the ratio of Cu and Sn in the powder of formula (1) is 1.0-35.0, preferably 5.0-25.0, more preferably 6.0-18.0, and even more preferably 7.0-12.0.
  • Tin (Sn) can be introduced as either a CuSn- or FeSn-based alloy produced via water, air or gas atomization, diffusion-bonding or any other market-available product of this kind, as Sn-based alloy or elemental Sn powder manufactured via air, gas atomization or other customary technologies, or as a combination of both.
  • Nickel is used to adjust the overall hardness level of the bond, given its solid solution strengthening in Fe and Cu and the well-known spinodal precipitation hardening in Cu-Sn-Ni system.
  • an essentially Ni-free product within the scope of the invention may still be a viable solution; for harder, more difficult to saw materials a stronger bond is required, and Ni addition is a very effective way to accommodate this demand, up to a saturation point.
  • Its content "e” shall thus be 0,01 ⁇ e ⁇ 15.
  • Nickel can be added either as elemental Ni in the form of water, air or gas atomized, electrolytic, carbonyl or any other market-available powder, or as Ni-based, FeNi-based, CoNi-based or CuNi-based alloy.
  • the content of Ni in the present composition is 0.01-15.0, preferably 0.1-12.0, more preferably 1.0-9.0, even more preferably 1.5-7.5, and yet more preferably 2.0-6.5.
  • Boron (B) and chromium (Cr) are notorious strong carbide formers and have already been included in formulations for diamond tool bonds to improve diamond retention by carbide formation on its surface, which serve as interface between the metallic bond and the matrix. They are typically added as fine elemental powders or sometimes as tool steels, also together with other carbide formers as Mn, Mo, W, V (see, e.g., J. Konstanty, Powder Metallurgy diamond tools, Elsevier 2005, p. 55 ; L. Duan, Metals 2018, pp. 4-5 ). They suffer however from several limitations.
  • a key finding of the inventive mix is to have found a way to successfully incorporate such carbide formers while improving at the same time diamond bonding and overall mechanical strength, without substantially affecting the free sintering capability.
  • This alloy system has been known for many years in the hardfacing industry (see e.g. A.A. Sorour, PhD thesis, Dept. of Mining and Materials Engineering, McGill University Montreal, April 2014 ), where such alloys are deposited by PTA, HVOF, MIG welding, Plasma Spray, etc. as anti-wear coatings.
  • Microstructure is composed of a Fe-based matrix (microhardness ⁇ 600 HV) with a dispersion of lamellar chromium-iron borides (Fe,Cr) 2 B (microhardness ⁇ 2.400 HV).
  • Fe-B system forms a eutectic at 4 wt.-% B with melting temperature of 1,174°C, down from 1,538°C for pure iron.
  • melting point is 2,092°C.
  • B has thus a double role of hardener and melting agent. In the context of the invention, this renders the powder much more sinter-active than elemental B, and by diluting it in Fe also less oxidation-sensitive.
  • Other typical additions are Si and Mn (Fe matrix hardening), Mo and V (carbide formers), Ni (better corrosion resistance thanks to austenitization on Fe-matrix).
  • FeCrBC-based pre-alloys are typically manufactured via atomization methods, either water, air, gas or a combination thereof.
  • Typical but not exclusive compositions in the hardfacing industry are Fe, 10-35% Cr, 3-5% B, 0,5-2,5% C, 0-20% Ni, 0-5% Si, 0-5% Mn, plus other possible additions of Mo, V, W, Nb, N.
  • Total boron and chromium content in the inventive mix, introduced via FeCrBC alloy, shall be balanced in order to avoid on one side ineffectiveness, and on the other side excessive embrittlement and oxidation sensitivity.
  • the content of B in the present composition is 0.02-1.0, preferably 0.05-0.70, more preferably 0.07-0.50, and even more preferably 0.10-0.30.
  • the content of Cr in the present composition is 0.10-4.0, preferably 0.20-3.0, more preferably 0.30-2.5, even more preferably 0.35-1.5, and yet more preferably 0.40-0.90.
  • the content of C in the present composition is 0.01-1.0, preferably 0.05-0.8, more preferably 0.08-0.6, still more preferably 0.10-0.50, and even more preferably 0.12-0.40.
  • the above described constituents shall be mixed according to usual procedures familiar to those skilled in the art, to create a homogeneous, agglomerate-free dispersion.
  • the precise mixing method is not seen as a critical aspect of the invention; it may involve, without being limited to, double-cone mixer, rotating cylinder, "turbula mixer” or any other device, with or without mixing aids. Ball milling may also be employed in this phase.
  • the mixture may then be admixed with an organic binder and other pressing aids to be granulated, or directly mixed with the quantity and grade of diamonds according to required application; this step may also occur at the same time the single constituents are brought together.
  • the bond - diamond mix is then cold pressed, typically under 200-300 MPa pressure. If the hot-pressing route is selected, the bond - diamond mix may be directly fed to the graphite die.
  • the present metal powder composition is mixed with diamonds (typically 5-10 vol-%), granulated and then cold pressed.
  • the composite is then consolidated close to full density via hot pressing or free sintering processes.
  • a graphite die is resistance-heated thus allowing the simultaneous application of heat and pressure.
  • Typical conditions are temperatures of 650-900°C, preferably 700-850°C, and more preferably 750-800°C, and pressures of 20-45 MPa, preferably 25-40 MPa, and more preferably 30-35 MPa.
  • the pressing may be conducted for e.g. 1-10 minutes, such as 2-8 or 3-5 minutes in air, inert gas or under vacuum.
  • hot pressing at 780-850°C and 35 MPa for 3 minutes under air/N 2 /vacuum is a common process in the industry.
  • Free sintering is the "standard" sintering process on a belt furnace. Typical conditions are 850-1,000°C, preferably 900-950°C, and more preferably 910-930°C for 30-120 minutes, typically 45-90 minutes, such as 60 minutes, under N 2 + H 2 . This process has become widespread for wire beads thanks to higher throughput. Such beads have also to be brazed to a steel sleeve in a second step or by using self-brazing matrixes.
  • the bond - diamond mix is then consolidated via hot-pressing, free sintering, hot isostatic pressing (HIP) or any of the conventional techniques known to those skilled in the art. No complicated extra steps nor special equipment, atmospheres, etc. are required.
  • free sintering consolidation the inventive product is particularly attractive, because of relatively low linear shrinkage required to reach near full density, in comparison to traditional pre-alloys. This descends directly from its better compressibility, which means it already starts from a higher density (around 77 % of theoretical value, while for pre-alloys around 60% is typical; see, e.g., J. M. Sanchez, Powder Metallurgy Powder Metallurgy 2014, Vol. 56, p. 362-373 ) and thus less shrinkage is required to reach the same final value.
  • the chart shown in Figure 1 illustrates this relationship. This allows for a very significant improvement in dimensional precision of the sintered components and thus reduced scrap rate.
  • Table 1 Composition of inventive mixtures 1' and 2' Content (%) Mix Fe WA Feco C Cu Sn Ni FeCrBC 1' 27,90 31,47 0,03 32,36 2,81 2,30 3,13 2' 25,46 28,71 0,15 31,23 2,72 5,70 6,04
  • Tensile bars according to ISO norm 2740 and weighing around 14 g each are compacted for Mix 1 and Mix 2 at 200, 300 or 400 MPa. Density is then measured via geometric method, by measuring bar dimensions with micrometer. Percentage density is calculated based on theoretical values, respectively 8,19 g/cm 3 form Mix 1 and 8,20 g/cm 3 for Mix 2 and subtracting the 0,60% lubricant contribution to weight. Table 2 presents the results of compressibility curves; it can be readily seen that the inventive products can be compacted to a relatively high density around 76% of theoretical values, even reaching 80% and above with 300 MPa.
  • T max is the sintering i.e. dwell temperature and, in this case, was set to 890°C, 910°C, 930°C or 950°C.
  • Test and TRS bars are sintered together under such conditions on steel trays, then after Step 3 the trays are manually moved to the forward zone of the furnace and left to cool naturally for 60 minutes (Step 4), before being taken out and spontaneously further cooled to room temperature.
  • Atmosphere is 40% H 2 and 60% N 2 , with total flow of 370 1/h.
  • Table 3 Description of sintering cycle for Example 1 Step 1 2 3 4
  • the sintered components are subjected to the following investigations. Dimensional change ⁇ L% is evaluated by taking the length of sintered tensile bars and expressing it as percentage variation to die cavity length of 89,40 mm. Density is assessed using water displacement method (Archimedes method) for all sintered components. Hardness is measured on the surface of tensile bars after polishing with #320 sand paper, according to ISO 6506 using a Brinell 2,5 mm spherical indenter and 187,5 kg load. Tensile properties (tensile strength Rm, 0,20% yield strength Rp 0,2 , plastic elongation at fracture A%) are assessed on a Zwick machine according to DIN EN ISO 10002/2000, with 10 mm/min crosshead speed.
  • Bending strength is measured for sintered TRS bars according to DIN EN ISO 7438/2000, under 3-points bending with support span of 25 mm and 10 mm/min crosshead speed.
  • the diamond acts as a stress concentrator and a discontinuity in the material, it invariably leads to a lower bending strength, particularly in case of discontinuous interface with metal matrix, brittle phase formation, local development of gases from reduction reactions, etc.
  • Table 4 shows the results for the inventive mixtures Mix 1 and Mix 2.
  • a density above 96% of theoretical can be reached within a wide processing window above 900°C, particularly between 910°C and 930°C which are typical processing temperatures for the free sintering of diamond tools.
  • Tensile properties are on par or even superior with what reported in scientific literature for pre-alloyed grades (see, e.g., A. M. Mancisidor et al., "Effect of the sintering atmosphere on the densification, mechanical properties and diamond stability of prealloyed diamond impregnated composites obtained by free-sintering", International Powder Metallurgy Congress and Exhibition, Euro PM 2013 ).
  • FIG. 2 SEM analysis of diamonds on fracture surface are shown in Fig. 2 .
  • the SEM photographs confirm a high compatibility with the metal bond. Edges remain sharp, without any sign of degradation up to 930°C.
  • the fractured spots observable on 930°C pictures are an indication of strong matrix - diamond interfacial bonding, with local preferential rupture path going through the stone. Some graphitization starts to occur for Mix 1D at 950°C, while Mix 2D can still well preserve the stones even at this relatively high temperature.
  • Can filling factor is around 33 %. A homogeneous mixture of the constituents is thus obtained, total weight 200 g for each mixture. It shall be noticed that Mixture 4' is not according to the invention, belonging H13 steel not to FeCrBC family. Table 6: Composition of mixtures 3' (invention)' and 4' (comp.) Content in % Mix Fe WA Feco C Cu Sn Ni FeCrBC H13 3' 22,71 28,41 0,14 34,96 3,04 5,00 5,70 0,00 4' 25,58 25,58 0,14 34,96 3,04 5,00 0,00 5,70
  • Test and TRS bars are sintered together under such conditions on steel trays, then after Step 3 the trays are manually moved to the forward zone of the furnace and left to cool naturally for 60 minutes (Step 4), before being taken out and spontaneously further cooled to room temperature. Atmosphere is 20% H 2 and 80% N 2 , with total flow of 290 1/hour.
  • Table 7 Sintering cycle for Comparative Example 1 Step 1 Step 2 Step 3 Step 4 Temperature [°C] 400 400 ⁇ Tmax 930 Tmax ⁇ 300 Dwelling time [min] 15 * 60 60 Heating rate [°C/h] * 300 * * *
  • Table 9 Sintering at 930°C for Mix 3 (inv.) and Mix 4 (comp.) Mix Without diamonds With Diamonds % ⁇ R [%] Sinter density oR Sinter density ⁇ R [g/cm 3 ] [%] [MPa] [g/cm 3 ] [%] [Mpa] 3 7,69 96,3 1189 7,73 96,8 821 69 4 7,91 98,8 1115 7,91 98,8 778 70
  • Mixture 5' and 6' are not according to the invention, belonging to FeCr 13 V 6 C 3,7 steels and not to the FeCrBC family.
  • Table 10 Composition of comparative mixtures 5' and 6' Content (%) Mix Fe WA Feco C Cu Sn Ni FeCrVC 63 ⁇ m FeCrVC 30 ⁇ m 5' 23,93 23,93 0,15 36,80 3,20 - 12,0 0,00 6' 23,93 23,93 0,15 36,80 3,20 - 0,00 12,0

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)
  • Carbon And Carbon Compounds (AREA)
  • Crystals, And After-Treatments Of Crystals (AREA)
EP19203219.1A 2019-10-15 2019-10-15 Premix alloy powders for diamond tools Active EP3808864B1 (en)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP19203219.1A EP3808864B1 (en) 2019-10-15 2019-10-15 Premix alloy powders for diamond tools
ES19203219T ES2919199T3 (es) 2019-10-15 2019-10-15 Polvos de aleación de premezcla para herramientas de diamante

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP19203219.1A EP3808864B1 (en) 2019-10-15 2019-10-15 Premix alloy powders for diamond tools

Publications (2)

Publication Number Publication Date
EP3808864A1 EP3808864A1 (en) 2021-04-21
EP3808864B1 true EP3808864B1 (en) 2022-05-18

Family

ID=68468537

Family Applications (1)

Application Number Title Priority Date Filing Date
EP19203219.1A Active EP3808864B1 (en) 2019-10-15 2019-10-15 Premix alloy powders for diamond tools

Country Status (2)

Country Link
EP (1) EP3808864B1 (es)
ES (1) ES2919199T3 (es)

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102021114399A1 (de) 2021-06-03 2022-12-08 Fraunhofer-Gesellschaft zur Förderung der angewandten Forschung eingetragener Verein Verfahren zur Herstellung von Werkzeugen, bei denen zumindest ein Arbeitsbereich mit Hartstoffpartikeln, die in einen metallischen Matrixwerkstoff eingebettet sind, ausgebildet ist
CN114134381B (zh) * 2021-12-06 2022-06-21 中南大学 一种耐磨多主元合金-金刚石复合材料及其制备方法和应用
CN115889782A (zh) * 2022-03-16 2023-04-04 浙江省永康市金都工贸有限公司 一种花岗石激光焊接锯片及其制作方法

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AU7528398A (en) * 1997-04-29 1998-11-24 N.V. Union Miniere S.A. Pre-alloyed copper containing powder, and its use in the manufac ture of diamondtools
ES2246049T3 (es) 2002-03-29 2006-02-01 Umicore Polvos aglutinantes prealeados.
FR2906739B1 (fr) 2006-10-04 2009-07-17 Eurotungstene Poudres Soc Par Poudre metallique prealliee, son procede d'obtention, et outils de coupe realises avec elle
CN105904597B (zh) * 2016-05-23 2018-06-08 江苏华昌工具制造有限公司 无压烧结干切片
CN108907179A (zh) * 2018-07-30 2018-11-30 铜陵长江金刚石工具有限责任公司 一种铁质金刚石钻头的制造方法

Also Published As

Publication number Publication date
ES2919199T3 (es) 2022-07-22
EP3808864A1 (en) 2021-04-21

Similar Documents

Publication Publication Date Title
EP3808864B1 (en) Premix alloy powders for diamond tools
KR100976731B1 (ko) 초고경도 복합 물질 및 그 제조 방법
EP2176019B1 (en) Iron-based powder combination and process for producing it
CA2355559C (en) Alloyed steel powder for powder metallurgy
EP1844172B1 (en) Iron-based powder combination
JP5535576B2 (ja) 鉄基焼結合金およびその製造方法並びに鉄基焼結合金部材
KR910007930B1 (ko) 연질복합금속분말과 그 제조방법
JP6259978B2 (ja) Ｎｉ基金属間化合物焼結体およびその製造方法
CN108085576A (zh) 一种钢结TiCN基硬质合金的制备方法
AU708686B2 (en) Method of powder metallurgical manufacturing of a composite material
Romanski et al. Ball-milled Fe-Ni and Fe-Mn matrix powders for sintered diamond tools
JP2001089823A (ja) 複硼化物系硬質焼結合金及びその合金を用いた樹脂加工機械用スクリュー
EP0200691B1 (en) Iron-based powder mixture for a sintered alloy
EP3722022B1 (en) A pre-alloyed water atomized steel powder
JP4121383B2 (ja) 寸法精度、強度および摺動特性に優れた鉄基燒結合金およびその製造方法
JPH10273701A (ja) 高強度を有する炭化タングステン基超硬合金の製造方法
RU2327547C1 (ru) Способ получения порошка на железной основе (его варианты)
JPH07188859A (ja) 粉末ハイス鋼
JPH1053823A (ja) 高強度を有する炭化タングステン基超硬合金の製造方法
JP2016145418A (ja) 鉄基焼結合金およびその製造方法
JPS6046170B2 (ja) 鉄粉末の液相焼結に用いる銅合金
EP0835329A1 (en) Hi-density sintered alloy and spheroidization method for pre-alloyed powders
CN108034881A (zh) 一种钢结TiCN基硬质合金及应用
RU2327548C1 (ru) Способ получения порошка на железной основе (его варианты)
JPS6119756A (ja) 焼結高速度綱の製造方法

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE APPLICATION HAS BEEN PUBLISHED

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20211013

RBV Designated contracting states (corrected)

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 32/00 20060101ALN20211202BHEP

Ipc: B22F 5/00 20060101ALN20211202BHEP

Ipc: C22C 38/56 20060101ALI20211202BHEP

Ipc: C22C 38/54 20060101ALI20211202BHEP

Ipc: C22C 38/04 20060101ALI20211202BHEP

Ipc: C22C 38/32 20060101ALI20211202BHEP

Ipc: C22C 38/18 20060101ALI20211202BHEP

Ipc: C22C 38/16 20060101ALI20211202BHEP

Ipc: C22C 33/02 20060101ALI20211202BHEP

Ipc: C22C 26/00 20060101ALI20211202BHEP

Ipc: C22C 1/05 20060101AFI20211202BHEP

INTG Intention to grant announced

Effective date: 20211217

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 32/00 20060101ALN20211206BHEP

Ipc: B22F 5/00 20060101ALN20211206BHEP

Ipc: C22C 38/56 20060101ALI20211206BHEP

Ipc: C22C 38/54 20060101ALI20211206BHEP

Ipc: C22C 38/04 20060101ALI20211206BHEP

Ipc: C22C 38/32 20060101ALI20211206BHEP

Ipc: C22C 38/18 20060101ALI20211206BHEP

Ipc: C22C 38/16 20060101ALI20211206BHEP

Ipc: C22C 33/02 20060101ALI20211206BHEP

Ipc: C22C 26/00 20060101ALI20211206BHEP

Ipc: C22C 1/05 20060101AFI20211206BHEP

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602019015051

Country of ref document: DE

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1493196

Country of ref document: AT

Kind code of ref document: T

Effective date: 20220615

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2919199

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20220722

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG9D

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20220518

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220919

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220818

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220819

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220818

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220918

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602019015051

Country of ref document: DE

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

26N No opposition filed

Effective date: 20230221

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220518

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221015

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221031

REG Reference to a national code

Ref country code: AT

Ref legal event code: UEP

Ref document number: 1493196

Country of ref document: AT

Kind code of ref document: T

Effective date: 20220518

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221015

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: IT

Payment date: 20230913

Year of fee payment: 5

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: BE

Payment date: 20230918

Year of fee payment: 5

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: ES

Payment date: 20231103

Year of fee payment: 5

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20230822

Year of fee payment: 5

Ref country code: CH

Payment date: 20231102

Year of fee payment: 5

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220511

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220511

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20191015

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20231015

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20231015

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20231015