EP1769098A1 - Feuillard d'acier pour spatule de peinture, spatule d'application et racloir de crepage, et procede de metallurgie des poudres pour le realiser - Google Patents

Feuillard d'acier pour spatule de peinture, spatule d'application et racloir de crepage, et procede de metallurgie des poudres pour le realiser

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Publication number
EP1769098A1
EP1769098A1 EP05772787A EP05772787A EP1769098A1 EP 1769098 A1 EP1769098 A1 EP 1769098A1 EP 05772787 A EP05772787 A EP 05772787A EP 05772787 A EP05772787 A EP 05772787A EP 1769098 A1 EP1769098 A1 EP 1769098A1
Authority
EP
European Patent Office
Prior art keywords
steel
steel strip
strip according
composition
thickness
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.)
Withdrawn
Application number
EP05772787A
Other languages
German (de)
English (en)
Inventor
Manfred DAXELMÜLLER
Helmut Ponemayr
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.)
Voestalpine Precision Strip GmbH
Original Assignee
Voestalpine Precision Strip 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 Voestalpine Precision Strip GmbH filed Critical Voestalpine Precision Strip GmbH
Publication of EP1769098A1 publication Critical patent/EP1769098A1/fr
Withdrawn legal-status Critical Current

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Classifications

    • 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
    • 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
    • B22F5/006—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of flat products, e.g. sheets
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D9/18—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for knives, scythes, scissors, or like hand cutting tools
    • 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
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • 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
    • C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01G—PRELIMINARY TREATMENT OF FIBRES, e.g. FOR SPINNING
    • D01G3/00—Roughening of fibres
    • D—TEXTILES; PAPER
    • D21—PAPER-MAKING; PRODUCTION OF CELLULOSE
    • D21G—CALENDERS; ACCESSORIES FOR PAPER-MAKING MACHINES
    • D21G3/00—Doctors
    • D21G3/005—Doctor knifes
    • 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
    • B22F2003/248—Thermal after-treatment
    • 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
    • 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
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12014—All metal or with adjacent metals having metal particles

Definitions

  • the invention relates to a cold-rolled steel strip having a thickness of 0.05 to 1.2 mm, which is used as a material for the production of doctor blades, applicator blades and creping doctor.
  • doctor blades or doctor blades are used in the form of thin, long knives to coat the paper web with a coating slip. These knives are pressed against the moving paper web, whereby a counterpressure is usually provided by a counter roll or a knife on the opposite side of the paper web if a double-sided coating is to be carried out.
  • the application knife must be straight if a uniform coating of the best quality is to be achieved.
  • the usual specification states that the machined edge of the applicator may not deviate more than 0.3 mm per 3000 mm applicator length from the complete straightness.
  • a steel alloy In order to meet these requirements, a steel alloy must be selected which prevents the bands from forming during hardening and tempering when the steel strips are subjected to these processes. It is known that in this respect alloy steels pose more problems than unalloyed steels, and this is especially true for steel alloys containing several different interacting alloying elements. Consequently, the most common material for order knives is still lenstoffstahl.
  • a typical composition of such a steel is, for example, (in% by weight) 1.00% C, 0.30% Si, 0.40% Mn, 0.15% Cr and the remainder iron and impurities in normal proportions.
  • Martensitic stainless steel is also used for the production of commissioned knives, eg the steel with the composition (in% by weight) 0.38% C, 0.5% Si, 0.55% Mn, 13.5% Cr, 1 , 0 Mo and the rest iron and impurities in normal proportions.
  • creping scrapers are used under the same conditions as described above in order to obtain a specific creping of the paper. High demands are also placed on the straightness of the working edge.
  • band-shaped coating tools are used, which are known as putties. They are similar to those used in the paper industry. These spatula must also meet high requirements regarding their straightness. The same material is used for both spatulas and applicators.
  • Application knives are highly stressed when using abrasive pigments in the material applied to the paper surface, as well as by the base paper, and worn at the edge.
  • Spreading knives are also heavily stressed by the color pigments in the order ink which are applied by the doctor blades. Accordingly, it is desirable that both applicator blade and doctor blade have a high abrasion resistance and consequently a long service life.
  • EP 0 672 761 B1 describes a steel which has the following composition (in% by weight) 0.46% -0.70% C, 0.2% -0.5% Si, 0.1 % - 2.0% Mn, 1.0% - 6.0% Cr, 0.5% - 5% Mo, 0.5% - 1.5% V, max. 0.01% B, max. 1.0% Ni, max. 0.2% Nb and the balance iron and impurities in the normal proportions.
  • the steel is suitable for the production of thin cold-rolled strips and, in its hardened and tempered state, can be used for the production of applicator and / or doctor blades.
  • the cold rolling process comprises a hardening step with an austenitization at 1000 ° C., followed by an annealing step in a lead bath at a temperature between 240 ° C. and 270 ° C.
  • Application and / or doctor blades made from this material have good abrasion resistance and straightness and their lifespan is 12 - 16 hours.
  • alloyed steel can be higher than that of non-alloyed steel. This is advantageous for certain tool and construction steels.
  • Some examples of these are the alloy steels described in JP-A-61/41749 and in US 4,743,426 and US 2,565,264 which are used for guide pins in plastic molds or hot-forming steels, e.g. are designed for high temperature aluminum extrusion dies as well as turbine blades, forging tools, cutting tools and similar products, and are made from billet or bar stock.
  • a bimetal coating blade is proposed.
  • the carrier band of the coating blade consists of a tough elastic steel on which an abrasion-resistant strip of HSS is applied in order to increase the stability of the coating blade.
  • These bimetal coating blades have disadvantages in terms of strength in the transition carrier tape - edge due to the material differences. Furthermore, such a bimetal coating blade is very expensive to manufacture and therefore expensive.
  • the applicator blade and doctor blade are first hot rolled from a block into a hot strip, which is then cold rolled to a steel strip having a thickness of 0.05 mm - 1.2 mm and a width of 10 mm - 250 mm.
  • a steel strip having a thickness of 0.05 mm - 1.2 mm and a width of 10 mm - 250 mm.
  • a steel strip for the production of doctor blades, applicators or creping doctor having a Stahlzu ⁇ composition comprising in percent by weight
  • the steel strip is produced using a powder metallurgy process.
  • the powder metallurgy manufacturing process can produce a steel of the above composition which has a high carbide content yet can be formed into a steel strip for doctor, applicator or creping doctor without embrittlement or cracking.
  • doctor blades, doctor blades and creping doctor are summarized under the term "knife”.
  • a steel strip according to the invention has a large number of small carbide crystals, so that the knives produced therefrom wear uniformly at their edge and no scoring occurs in the paper or streaking in the paper coating.
  • knives of the steel strip according to the invention have a high wear resistance, without a complex and expensive manufacturing process was used. The strength disadvantages that occur with a Bimetallsteichklinge can not occur in the uniform material of the steel strip according to the invention.
  • the steel strip according to a thickness of 0.05 - 1.2 mm, and / or a width of 10 - 250 mm.
  • the steel strip is produced using a cold rolling process. Due to the fine grain of the structure, the cold rolling on the above. Dimensions only possible.
  • the steel composition cumulatively or alternatively comprises the following components in the following parts by weight:
  • the steel strip preferably has a working edge which has a hardness of 500-600 HV, preferably 575-585 HV and / or a straightness of 0.3 mm / 3000 mm strip length.
  • the working edge is hardened, preferably laser beam-hardened. This has the advantage that a very targeted introduction of heat energy into the material is possible without the use of a vacuum environment.
  • An applicator blade made of a steel strip according to the invention preferably has a thickness of 0.25-0.64 mm.
  • a doctor blade made of a steel strip according to the invention preferably has a thickness of 0.15-1.0 mm.
  • a creping doctor made from a steel strip according to the invention preferably has a thickness of 0.25-1.2 mm.
  • the step of cold rolling is preferably carried out by means of edge supports.
  • a hardening step is carried out at a temperature of 950-1050 ° C., followed by an annealing step at a temperature of 550-650 ° C.
  • Cold rolling, curing and tempering preferably take place in a continuous process.
  • the hardening step comprises a cooling step, wherein the strip is cooled between cooling plates to a temperature of 150-25O 0 C.
  • the working edge of the belt is hardened, preferably by means of a load beam.
  • 1 is a three-dimensional view of a Stahlban ⁇ invention in the rolled up state
  • FIG. 2 shows a three-dimensional view of a partial section of a steel strip according to the invention for illustrating a first edge shape
  • FIG. 3 shows a three-dimensional view of a partial section of a steel strip according to the invention for clarifying the dimensions and a second one
  • FIG. 4 shows two schematic three-dimensional microscopically enlarged partial sections of the edge material of a steel strip, wherein on the left a steel strip * of the prior art and on the right a steel strip according to the invention is shown; and Fig. 5 shows two microscopically enlarged grinding Sparaurhahmen of Kantenmateri ⁇ than a steel strip, on the left a steel strip of the prior art and on the right an erf ⁇ ndungswashes steel strip is shown.
  • the invention relates to the use of a special Stahl ⁇ alloy with a special composition for the production of knives (applicator and doctor blade, scraper, creping doctor, blades, doctor blade, scraper) in the form of cold-rolled, hardened and annealed tapes.
  • Fig. 1 shows a three-dimensional view of a erfmdungs contemporary steel strip 1 in the rolled up state, as provided for shipping.
  • FIG. 3 shows the dimensions.
  • the width B is between 10 and 250 mm
  • the thickness of the applicator blades is between 0.05 and 1.2 mm and, in a typical case, between 0.25 and 0.64 mm.
  • the thickness in a typical case is between 0.15 and 1.0 mm.
  • Creping scrapers have a typical thickness of 0.25 - 1.2 mm.
  • the machined edge 20 of a blade can either be straight, ie have a 90 ° angle.
  • the edge 10 can also be bevelled, as shown in FIG. This is an edge shape that is also used for applicator and doctor blades.
  • carbon should be present in the steel in sufficient quantities to give it a basic hardness sufficient to withstand the pressure against the paper web or inking roll without being subjected to permanent deformation, and also during annealing to form MC carbides.
  • MC carbides cause precipitation hardening and thus improved abrasion resistance of the edge.
  • the carbon content should therefore be at least 1% C and preferably 1.50%.
  • the maximum carbon content is 3% C.
  • Vanadium should be present in the steel in order to form very small MC carbides during the tempering or annealing by precipitation. It is believed that these MC carbides are the main reason for the surprisingly good abrasion resistance of the doctor blades of the present invention.
  • the carbides have a submicroscopic size, which means a maximum size of the order of magnitude of between 1 and 3 ⁇ m.
  • the vanadium content should be at least 4% V. The vanadium content should not exceed 10% V.
  • the chromium content should whom 'gstens 6% Cr, preferably at least 6.5% Cr betra ⁇ gene to impart sufficient hardenability to the steel, ie it quenching in air or after austenitization in martensite wah ⁇ rend umzu ⁇ form.
  • chromium is also carbide-forming, which is why it competes with vanadium for the carbon in the steel matrix.
  • chromium carbides do not form the precipitation hardening, which is desirable and can be formed by the vanadium in the above-mentioned amounts. Chromium in larger amounts also creates a higher risk of retained austenite.
  • the chromium content in the steel is limited to 10%, preferably to at most 8.5%.
  • the molybdenum content should be at least 1%, so that it can form MC carbides together with vanadium and can positively contribute to the formation of these carbides. Since molybdenum is present in the MC carbides, they dissolve more easily during austenitization when curing takes place and then form part of the MC carbides formed during annealing. However, the molybdenum content must not be so high that disadvantageous amounts of molybdenum carbides are formed which, like chromium carbides, are unstable and grow at high temperatures. The molybdenum content should therefore be limited to 2%, preferably to 1.5%.
  • Molybdenum can be replaced in the usual way completely or partially by twice the amount of tungsten. Therefore, in a preferred embodiment, the alloy composition should not have tungsten exceeding an impurity level.
  • the manganese content in the steel is limited to 1% and, like chromium, contributes to giving the steel the desired hardenability.
  • the manganese content is preferably 0.4- 0.5% Mn.
  • the silicon content should be at least 0.8% in order to increase the carbon activity in the steel and to accelerate the precipitation of the small vanadium carbides during annealing.
  • the increased carbon activity can also lead to a faster coarsening of the carbides, resulting in a faster softening of the steel.
  • the tempering curve is shifted to the left, and the hardness maximum is shifted upward when the silicon content is high.
  • the steel should not contain more than at most 1.1% silicon and preferably not more than 1.0% silicon.
  • Nickel does not provide any positive contribution to the steel in the desired application. Nickel may affect the heat treatment of the product Steel. Therefore, the steel is best not more nickel than at Verunreini ⁇ supply level.
  • the steel contains essentially nothing but iron.
  • Other elements including, for example, aluminum, nitrogen, copper, cobalt, titanium, niobium, sulfur and phosphorus are present in the steel only as impurities or as unavoidable minor elements.
  • three different steel alloys were powder metallurgically produced, cold rolled and tested with good results.
  • the three alloys were cold rolled into thin strips of 0.05-1.2 mm thickness and 10-250 mm width and can be used for the production of doctor blades, calipers and creping doctor blades.
  • the nominal compositions of these steel alloys were as follows:
  • Koh ⁇ should lenstoff present in sufficient amounts to give it a basic hardness, sufficient to endure being 'pressed against the paper web or ink application roll, respectively, without suffering permanent deformations in the steel, as well as to form MC carbides during annealing.
  • MC carbides cause a precipitation hardening and thus an improved Abrasion resistance of the edge.
  • the carbon content should therefore be at least 1.0% C and preferably 1.2%.
  • the maximum carbon content is 2.5% C, preferably 2.3% C.
  • Vanadium should be present in the steel in order to form very small MC carbides during the tempering or annealing by precipitation. It is believed that these MC carbides are the main reason for the surprisingly good abrasion resistance of the doctor blades of the present invention.
  • the carbides have a submicroscopic size, which is a maximum size of the order of 1 .mu.m-3 .mu.m. means.
  • the vanadium content should be at least 2.5% V, preferably at least 3.0% V.
  • the vanadium content should not exceed 7% V and preferably the steel contains at most 6.5% vanadium.
  • the chromium content is lower.
  • the chromium content should be at least 4% Cr in order to lend sufficient hardenability to the steel, i. to transform it into martensite during quenching in air or after austenitisation.
  • chromium is also carbide-forming, which is why it competes with vanadium for the carbon in the steel matrix.
  • the chromium content in the steel can be 5%. The nominal proportion is approximately 4.2% Cr.
  • the molybdenum content should be at least 4%, so that it can form MC carbides together with vanadium and can positively contribute to the formation of these carbides. Since molybdenum is present in the MC carbides, they dissolve more easily during austenitization when curing takes place and then form part of the MC carbides formed during annealing. However, the molybdenum content must not be so high that disadvantageous amounts of molybdenum carbides are formed which, like chromium carbides, are unstable and at high temperatures Temperatures are growing. The molybdenum content should therefore be limited to 8% Mo, preferably between 5-7% Mo, in this second embodiment.
  • Molybdenum can be replaced in the usual way completely or partially by twice the amount of tungsten. Tungsten improves the abrasion resistance, increases the hardening temperature and improves the heat resistance. According to this second embodiment, the steel contains 6-7% W, preferably about 6.4-6.5% tungsten.
  • the manganese content in the steel is limited to 1% and, like chromium, contributes to giving the steel the desired hardenability.
  • the manganese content is preferably 0.3% Mn.
  • the silicon content should be at least 0.8% in order to increase the carbon activity in the steel and to accelerate the precipitation of the small vanadium carbides during annealing.
  • the increased carbon activity can also lead to a faster coarsening of the carbides, resulting in a faster softening of the steel.
  • the tempering curve is shifted to the left, and the hardness maximum is shifted upward when the silicon content is high.
  • the steel should not contain more than 0.8% silicon at most and preferably not more than 0.5% silicon.
  • Nickel does not provide any positive contribution to the steel in the desired application field. Nickel may affect the heat treatment of the steel. Therefore, in this second embodiment, the steel is best not containing more nickel than at the impurity level.
  • the steel contains cobalt in an amount of at least 8%.
  • Cobalt improves the hot workability of the steel.
  • cobalt makes the steel more brittle and increases the formation hardening in the cold forming operations. Therefore, the steel should not more than 12% cobalt, preferably not more than 11%. Improved hot workability is not a critical property for the steel, and therefore this second embodiment of the invention essentially does not contain cobalt.
  • the steel contains essentially nothing but iron.
  • Other elements including, for example, aluminum, nitrogen, copper, cobalt, titanium, niobium, sulfur and phosphorus are present in the steel only as impurities or as unavoidable minor elements.
  • the applicator or doctor blade and the creping doctor are produced according to the vor ⁇ underlying invention as follows.
  • An alloy having the desired composition described above and in the claims is prepared using a powder metallurgy process.
  • the powder is mixed in the desired composition and compacted into compact blocks by hot isostatic pressing.
  • the blocks then become Hot rolled strips of thickness of about 3 - 3.5 mm.
  • the strips are cold rolled to a desired thickness of less than 1.2 mm.
  • Alter ⁇ nierend intermediate heating steps can be performed.
  • cold rolling is performed by means of edge supports. When the strip 1 has reached its final thickness T during the cold rolling, it is subsequently hardened and tempered in a continuous process.
  • the cold-rolled strips 1 of the first embodiment are cured using Austenitmaschine at a temperature of 950 ° C - 1050 ° C, followed by quenching between cooling plates to a temperature of 15O 0 C - 25O 0 C and a tempering or Annealing at 550 ° C.-650 ° C.
  • the cold-rolled strips 1 of the second embodiment are Verwen ⁇ dung austenitization at a temperature of 1000 0 C - hardened 1050 0 C, followed by quenching between cooling plates to a temperature of 150 0 C - 25O 0 C and tempering or annealing at 550 0 C - 65O 0 C.
  • the bands 1 can be dyed by annealing in an oxidizing atmosphere.
  • the bands 1 are cut to the correct length and width B, and the edge 10, 20 is processed by sizing and / or grinding to obtain the desired edge profile.
  • the working edge should have a straightness of 0.3 mm / 3000 mm strip length.
  • the flatness should be at least 0.3% of the nominal bandwidth according to the Pilhöjld standard.
  • the bands are characterized by working edges 10, 20, which have improved properties. In particular, they have an increased abrasion resistance in comparison to other tapes available today.
  • the working edge 10, 20 can be hardened by means of local heating of the edge region, for example by means of induction hardening.
  • curing by means of a high energy jet may also be used, for example laser, plasma or electron beam curing, which gives the working edge 10, 20 a certain hardened area which does not affect the straightness of the belt.
  • a laser beam is used for this purpose.
  • the working edge 10, 20 hardened in this way achieves an improved hardness of up to 630 HV, preferably 620 HV.
  • FIGS. 4 and 5 show microscopic enlargements of the microstructure of the working edge 10, 20.
  • the left-hand illustration in FIGS. 4 and 5 shows a structure 30 according to the prior art, which was produced by means of a conventional melting process.
  • the working edge 10, 20 wears, whereby the carbides 34, 36 wear less strongly than the surrounding material 32.
  • the carbides on the surface protrude from the rest of the structure, as in the case of the carbide with the reference numeral 36 is shown.
  • Such incident ⁇ standing carbides produce on the paper surface or the backing roll grooves or stripes in the coating of the paper, so that the blades must be replaced.
  • a structure 40 of a working edge 10, 20 according to the invention is shown on the right side of Fig. 4 and 5, a structure 40 of a working edge 10, 20 according to the invention is shown.
  • the structure 40 has the same steel composition. However, it was produced by means of a powder metallurgical process. This results in fine, well distributed carbides 44 which are embedded in the surrounding structure 42.
  • a working edge 10, 20 with such a structure 40 wears off evenly and without protruding carbides 36 and therefore does not lead to a scoring or banding.
  • the method according to the invention which makes it possible to successfully produce cold-rolled strips with widths of up to 250 mm, makes it possible for a plurality of narrow strips to be produced simultaneously.
  • a wide strip 1 is cut into several narrow strips before the edges 10, 20 are machined. In this way, for example, by means of a single cold rolling operation of a wide band two narrow bands can be obtained.

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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)
  • Manufacturing & Machinery (AREA)
  • Textile Engineering (AREA)
  • Coating Apparatus (AREA)
  • Paper (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Application Of Or Painting With Fluid Materials (AREA)
  • Powder Metallurgy (AREA)

Abstract

La présente invention concerne un feuillard d'acier (1) destiné à la réalisation de spatules de peinture, de spatules d'application ou de racloirs de crêpage, ayant une composition d'acier comprenant un pourcentage pondéral de 1 - 3 % de C, 4 - 10 % de Cr, 1 - 8 % de Mo, 2,5 - 10 % de V, le reste étant du fer et des impuretés en des proportions normales. Selon l'invention, le feuillard d'acier (1) est réalisé au moyen d'un procédé de métallurgie des poudres. L'invention a également pour objet des spatules de peinture, des spatules d'application ou des racloirs de crêpage réalisés à partir de ce feuillard d'acier, et un procédé pour les réaliser.
EP05772787A 2004-07-19 2005-07-07 Feuillard d'acier pour spatule de peinture, spatule d'application et racloir de crepage, et procede de metallurgie des poudres pour le realiser Withdrawn EP1769098A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102004034905A DE102004034905A1 (de) 2004-07-19 2004-07-19 Stahlband für Streichmesser, Auftragsmesser und Kreppschaber und pulvermetallurgisches Verfahren zu ihrer Herstellung
PCT/EP2005/007356 WO2006007984A1 (fr) 2004-07-19 2005-07-07 Feuillard d'acier pour spatule de peinture, spatule d'application et racloir de crepage, et procede de metallurgie des poudres pour le realiser

Publications (1)

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EP1769098A1 true EP1769098A1 (fr) 2007-04-04

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EP05772787A Withdrawn EP1769098A1 (fr) 2004-07-19 2005-07-07 Feuillard d'acier pour spatule de peinture, spatule d'application et racloir de crepage, et procede de metallurgie des poudres pour le realiser

Country Status (10)

Country Link
US (1) US7722697B2 (fr)
EP (1) EP1769098A1 (fr)
JP (1) JP2008506844A (fr)
KR (1) KR20070048197A (fr)
CN (1) CN100540710C (fr)
BR (1) BRPI0513482A (fr)
CA (1) CA2573630A1 (fr)
DE (1) DE102004034905A1 (fr)
TW (1) TW200611984A (fr)
WO (1) WO2006007984A1 (fr)

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US8635755B2 (en) 2010-04-13 2014-01-28 Daetwyler Swisstec Ag Method for producing doctor blades
EP2686481B1 (fr) * 2011-03-18 2017-07-12 PrimeBlade Sweden AB Outil en forme de lame et son procédé de fabrication
DE102013205597A1 (de) * 2013-03-28 2014-10-02 Voith Patent Gmbh Schaber
EP2896714B1 (fr) 2014-01-17 2016-04-13 voestalpine Precision Strip AB Lame de crêpage et son procédé de fabrication
ES2631186T3 (es) * 2014-12-10 2017-08-29 Voestalpine Precision Strip Ab Cuchilla de crepado revestida de cermet de larga duración
CN104805366B (zh) * 2015-05-20 2017-05-24 中南大学 一种粉末冶金低合金钢及其制备方法
EP3165367A1 (fr) 2015-11-04 2017-05-10 BTG Eclépens S.A. Racloir, agencement d'encrage et utilisation d'un racloir dans l'impression flexographique
US11167454B2 (en) 2017-01-13 2021-11-09 General Electric Company Method and apparatus for continuously refreshing a recoater blade for additive manufacturing
USD946841S1 (en) * 2017-10-20 2022-03-22 Gene David Ruble Cleaning implement
JP7255287B2 (ja) * 2019-03-28 2023-04-11 株式会社プロテリアル 炭素工具鋼鋼帯の製造方法
EP3936339A1 (fr) 2020-07-10 2022-01-12 Daetwyler Swisstec Ag Raclette traitée au laser
CN113502437A (zh) * 2021-07-02 2021-10-15 富奥威泰克汽车底盘系统成都有限公司 用于高强度钢板的冲压模具
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CN115821188B (zh) * 2022-12-21 2023-12-29 重庆宗申发动机制造有限公司 一种带有涂层的钛合金及其制备方法

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Also Published As

Publication number Publication date
DE102004034905A1 (de) 2006-04-13
CN100540710C (zh) 2009-09-16
US20080096037A1 (en) 2008-04-24
BRPI0513482A (pt) 2008-05-06
TW200611984A (en) 2006-04-16
CA2573630A1 (fr) 2006-01-26
JP2008506844A (ja) 2008-03-06
US7722697B2 (en) 2010-05-25
KR20070048197A (ko) 2007-05-08
WO2006007984A1 (fr) 2006-01-26
CN101128613A (zh) 2008-02-20

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