SE449758B - PROCEDURE FOR MANUFACTURING MELTALUMINUM PLATED STEEL PLATE - Google Patents
PROCEDURE FOR MANUFACTURING MELTALUMINUM PLATED STEEL PLATEInfo
- Publication number
- SE449758B SE449758B SE8100310A SE8100310A SE449758B SE 449758 B SE449758 B SE 449758B SE 8100310 A SE8100310 A SE 8100310A SE 8100310 A SE8100310 A SE 8100310A SE 449758 B SE449758 B SE 449758B
- Authority
- SE
- Sweden
- Prior art keywords
- temperature
- platinum
- rolled
- steel
- plated steel
- Prior art date
Links
- 238000000034 method Methods 0.000 title claims description 11
- 238000004519 manufacturing process Methods 0.000 title claims description 7
- 229910000831 Steel Inorganic materials 0.000 claims description 24
- 239000010959 steel Substances 0.000 claims description 24
- 230000003647 oxidation Effects 0.000 claims description 14
- 238000007254 oxidation reaction Methods 0.000 claims description 14
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 claims description 14
- 239000000203 mixture Substances 0.000 claims description 12
- 238000007747 plating Methods 0.000 claims description 10
- 229910052782 aluminium Inorganic materials 0.000 claims description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 7
- 229910052697 platinum Inorganic materials 0.000 claims description 7
- 238000000137 annealing Methods 0.000 claims description 6
- 238000004804 winding Methods 0.000 claims description 6
- 238000005054 agglomeration Methods 0.000 claims description 5
- 230000002776 aggregation Effects 0.000 claims description 5
- 230000001590 oxidative effect Effects 0.000 claims description 5
- 238000009849 vacuum degassing Methods 0.000 claims description 5
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 238000005554 pickling Methods 0.000 claims description 4
- 238000005096 rolling process Methods 0.000 claims description 4
- 238000002485 combustion reaction Methods 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 238000007670 refining Methods 0.000 claims description 3
- 238000005266 casting Methods 0.000 claims description 2
- 238000009749 continuous casting Methods 0.000 claims description 2
- 238000000746 purification Methods 0.000 claims description 2
- 239000000126 substance Substances 0.000 claims description 2
- 239000000463 material Substances 0.000 description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 6
- 238000012360 testing method Methods 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 4
- 239000010410 layer Substances 0.000 description 4
- 238000009792 diffusion process Methods 0.000 description 3
- 229910052760 oxygen Inorganic materials 0.000 description 3
- 239000000758 substrate Substances 0.000 description 3
- 230000004584 weight gain Effects 0.000 description 3
- 235000019786 weight gain Nutrition 0.000 description 3
- 238000005261 decarburization Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 229910001021 Ferroalloy Inorganic materials 0.000 description 1
- 229910000604 Ferrochrome Inorganic materials 0.000 description 1
- 229910000616 Ferromanganese Inorganic materials 0.000 description 1
- 229910001200 Ferrotitanium Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- DALUDRGQOYMVLD-UHFFFAOYSA-N iron manganese Chemical compound [Mn].[Fe] DALUDRGQOYMVLD-UHFFFAOYSA-N 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
Classifications
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- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Organic Chemistry (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Coating With Molten Metal (AREA)
- Heat Treatment Of Steel (AREA)
Description
449 758 2 tionen 3553g/75/ är känt ett förfarande för framställning av alumi- niumpläterad stålplåt vilket utmärker sig av, att man varmvalsar ett stål som i huvudsak innehåller 0,001-0,020 % C,f§_0,05 % Si, 0,05-0,H0 z Mn, o,1o-o,3o z cr, en effektiv 'ri-helt av o,o3-0,110 ß (totalt 'ri minus Ti i oxidform) och minst U ggr (C+N) %,f§ 0,006 % N,§L 0,020 % O, varvid resten utgörs av Fe och oundvikliga föroreningar, vid en temperatur av lägst 800°C, kallvalsar den varma rullen vid en reduk- tionsgrad av HO % eller mer, glödgar den valsade plåten vid 800-95000 och sänker ned plåten i ett A1-Si.1egeringsbadQÉ;10 % Si) som upprätt- nänee vid 614o-7oo°c i högst 10 min. . 445 758 2 3553g / 75 / is known a process for producing aluminum-plated steel sheet which is characterized by hot-rolling a steel which essentially contains 0.001-0.020% C, f§_0.05% Si, 0.05 -0, H0 z Mn, o, 1o-o, 30o z cr, an effective 'ri-hero of o, o3-0,110 ß (total' ri minus Ti in oxide form) and at least U times (C + N)%, f§ 0.006% N, §L 0.020% 0, the remainder being Fe and unavoidable impurities, at a temperature of not less than 800 ° C, cold rolling the hot roll at a degree of reduction of HO% or more, annealing the rolled sheet at 800-95000 and immerses the plate in an A1-Si.1 alloy bathQÉ; 10% Si) which is set up at 614o-7oo ° c for a maximum of 10 minutes. .
Den aluminiumpläterade stålplåt som uppnås medelst detta för- farande har en sträckgräns på 13-17 kp/mm2 och en töjning på ÄH-H7 % som kallvalsad plåt med 0,8 mm tjocklek. Idag är emellertid efterfrå- gan på mer lätt formbara material i stigande.The aluminum-plated steel sheet obtained by this method has a yield strength of 13-17 kp / mm2 and an elongation of ÄH-H7% as cold-rolled sheet with a thickness of 0.8 mm. Today, however, the demand for more easily formable materials is rising.
Olika sätt att möta denna efterfrågan har studerats, varvid framkommit idén att utnyttja följande tre åtgärder för uppnående av förbättrad aluminiumpläterad stålplåt som har god formbarhet med låg sträckgräns och mycket låg viktökning vid höåtemperaturoxidation. 1. För det första kan man sänka C och 0-halten i underlagsplåten av stål genom utnyttjande av vakuumavgasning och preliminär desoxida- tion med Al vid ståltillverkningsstadiet och därmed minska den Ti- halt som är nödvändig för att fixera C och N och reglera oxidbild- ningen. 9272 2. För det andra kan man minska Mn-halten, vilket ökar sträckgrän- senzoch tillsätta C, vilket sänker sträckgränsen. 3. För det tredje kan man befrämja agglomeringen och tillväxten av den utskilda Ti-karbiden genom upplindning vid en temperatur så hög som 700°C och sålunda förhindra hårdnande genom bildning av karbid av det Ti som satts till underlagsmaterialet. Agglomeringen av Ti-kar- biden kan ytterligare befrämjas genom värmning av den kallvalsade plåten till en temperatur av 85000 eller mer då den leds genom en di- rekt påföljande varmpläteringsanordning av glödningstyp med en icke- oxiderande ugn (i Japan allmänt benämnd pläteringsanordning av NOF- typ).Various ways of meeting this demand have been studied, giving rise to the idea of using the following three measures to achieve improved aluminum-plated steel sheet which has good formability with low yield strength and very low weight gain at high temperature oxidation. 1. First, the C and O content of the steel backing sheet can be lowered by using vacuum degassing and preliminary deoxidation with Al at the steelmaking stage, thereby reducing the Ti content necessary to fix C and N and regulate oxide formation. ningen. 9272 2. Secondly, you can reduce the Mn content, which increases the yield strength and add C, which lowers the yield strength. 3. Third, the agglomeration and growth of the precipitated Ti carbide can be promoted by winding at a temperature as high as 700 ° C and thus preventing hardening by forming carbide of the Ti added to the support material. The agglomeration of the Ti carbide can be further promoted by heating the cold-rolled sheet to a temperature of 85,000 or more as it is passed through a directly subsequent hot-type annealing furnace with a non-oxidizing furnace (in Japan commonly referred to as NOF type).
Föreliggande uppfinning utmärker sig dessutom av att materialets högtemperaturoxidationsbeståndighet förbättras genom kombinerad till- sättning av Ti och Cr.D v s viktökningen vid oxidation vid höga tempe- raturer minskas avsevärt genom avkolning av underlagsmaterialet, Och den förbättras ytterligare genom tillsättning av Ti. Orsakerna därtill är: 1) genom avkolning eller tillsättning av Ti förbättras järnmate- rialets renhet, och aluminiumskiktets Al diffunderar lätt in i Fe- »p 449 758 underlaget och ett Al-diffusionsskikt med utmärkt högtemperaturoxida- tionsbeständighet bildas. 2) Ti i materialet diffunderar mot ytan och bildar ett Ti-koncentrerat skikt under Al-diffusionsskiktet vid uppvärmning av materialet till hög temperatur, och sålunda förhindras vidare diffusion av Al in i det inre, varigenom ökningen i Al-koncen- trationen 1 ytskiktet bromsas och även det syre som trängt in i järnet fixeras.The present invention is further characterized in that the high temperature oxidation resistance of the material is improved by the combined addition of Ti and Cr.D. The weight gain in oxidation at high temperatures is considerably reduced by decarburization of the substrate material, and it is further improved by the addition of Ti. The reasons for this are: 1) by decarburization or addition of Ti, the purity of the iron material is improved, and the Al of the aluminum layer diffuses easily into the Fe- »p 449 758 substrate and an Al diffusion layer with excellent high temperature oxidation resistance is formed. 2) Ti in the material diffuses towards the surface and forms a Ti-concentrated layer below the Al diffusion layer when heating the material to a high temperature, and thus further diffusion of Al into the interior is prevented, thereby slowing down the increase in Al concentration in the surface layer. and also the oxygen which has penetrated into the iron is fixed.
Föreliggande uppfinning avser sålunda ett förfarande för framställning av smältaluminiumpläterad stálplàt med god form- barhet och god högtemperaturoxidationsbeständighet som lämpar sig för tillverkning av delar med komplicerad form för använd- ning vid höga temperaturer, t ex i avgasreningsanordningar för förbränningsmotorer, vid vilket ett stål med i huvudsak följande kemiska sammansättning: 0,001-0,020% C, 0,05-0,30% Mn, 0,05-0,50% Cr, 0,01-0,10% Al, och en halt av Ti av 0,10- O,§0% och minst 10 ggr procenthalten C, varvid resten ut- görs av Fe och oundvikliga föroreningar, framställs genom van- lig konverterraffinering och vakuumavgasning, stålet överförs till platiner genom vanlig gjutning och platinvalsning eller vanlig stränggjutning, platinerna varmvalsas kontinuerligt och * lindas upp till en rulle, den resulterande varma rullen efter vanlig betningsbehandling rullas ut och kallvalsas, den kall- valsade plåten värms till en temperatur av lägst 850°C och plä- teras med smält aluminium i en enligt Sendzimirmetoden arbetan- de pläteringsanläggning, vars andra glödgningsugn har icke- oxiderande atmosfär i stället för reducerande atmosfär, som utmärker sig av att upplindningen sker vid en temperatur av lägst 700°C, vilket befrämjar agglomerering och tillväxt av utskild Ti-karbid och därmed en god formbarhet hos plåten.The present invention thus relates to a process for the production of molten aluminum-plated steel sheet with good formability and good high-temperature oxidation resistance which is suitable for the manufacture of parts with a complicated shape for use at high temperatures, for example in exhaust gas purification devices for internal combustion engines. essentially the following chemical composition: 0.001-0.020% C, 0.05-0.30% Mn, 0.05-0.50% Cr, 0.01-0.10% Al, and a Ti content of 0.10 - 0, §0% and at least 10 times the percentage C, the remainder being Fe and unavoidable impurities, produced by ordinary converter refining and vacuum degassing, the steel is transferred to platinum by ordinary casting and platinum rolling or ordinary continuous casting, the platinums are continuously hot rolled and * wound up into a roll, the resulting hot roll after normal pickling treatment is rolled out and cold rolled, the cold rolled sheet is heated to a temperature of at least 850 ° C and plated with molten al uminium in a plating plant operating according to the Sendzimir method, whose second annealing furnace has a non-oxidizing atmosphere instead of a reducing atmosphere, which is characterized by the winding taking place at a temperature of at least 700 ° C, which promotes agglomeration and growth of separated Ti-carbide and thus a good formability of the plate.
Skälet varför upplindningstemperaturen definieras som minst 700°C är att vid en temperatur lägre än denna materialet till följd av agglomeringen och tillväxten av de Ti-utskiljningar som har bildats genom fixering av C vid Ti, icke mjukgöres tillräckligt, varigenom så- lunda ett av de utmärkande dragen för föreliggande uppfinning går för- lorat. Dessutom erfmrdras att den kallvalsade plåten i aluminíumpläte- ringsproduktionslinjen måste värmas vid lägst 850°C före den införs i pläteringsbadet, detta för att ge den kallvalsade plåten en sådan glödg- ningseffekt att,Ti-utskiljningarna ytterligare agglomeras till större 449 758 partiklar och sålunda gör materialet mjukare.The reason why the winding temperature is defined as at least 700 ° C is that at a temperature lower than this material due to the agglomeration and growth of the Ti precipitates which have been formed by fixing C to Ti, it is not sufficiently softened, thus one of the characteristic features of the present invention are lost. In addition, it is required that the cold-rolled sheet in the aluminum plating production line must be heated at least 850 ° C before it is introduced into the plating bath, in order to give the cold-rolled sheet such an annealing effect that the Ti precipitates are further agglomerated into larger 449,758 particles and thus the material softer.
Vid förfarandet enligt föreliggande uppfinning skiljer sig sammansättningen för underlagsstålet från den för underlagsstålen för förfarandet enligt den ovan nämnda japanska-patentskriften 353 175 (japanska patentpublikationen 55532/76 endast genom att stålet enligt föreliggande uppfinning innehåller avsiktligt till- satt Al. Förfarandet skiljer sig emellertid helt från det enligt ovannämnda uppfinning.In the process of the present invention, the composition of the support steel differs from that of the support steels of the process of the above-mentioned Japanese Patent 353 175 (Japanese Patent Publication 55532/76 only in that the steel of the present invention contains intentionally added Al. However, the process is completely different). from that of the above invention.
Uppfinningen skall nu beskrivas närmare nedan på basis av ex- perimentresultaten.The invention will now be described in more detail below on the basis of the experimental results.
Stålprover vars sammansättning anges i tabell 1 iordningställ- des genom konverterraffinering och vakuumavgasning. Götên utsattes för platinvalsning och kontinuerlig varmvalsning och de valsade pro- dukterna lindades upp till rullar vid olika temperaturer såsom anges i tabellen, varvid varma rullar med en tjocklek på 2,5 mm erhölls.Steel samples whose composition is given in Table 1 were prepared by converter refining and vacuum degassing. The ingots were subjected to platinum rolling and continuous hot rolling and the rolled products were wound up into rolls at different temperatures as indicated in the table, whereby hot rolls with a thickness of 2.5 mm were obtained.
Efter konventionell betning tillverkades av de varma rullarna kallval- sad plåt med en tjocklek av 0,8 mm..De sålunda iordningställda kall- valsade plåtarna värmdes vid varierande temperaturer och pläterades med aluminium (60 g/m2) medelst en direkt efterföljande varmpläterings- anordning av glödgningstyp med en ícke~oxiderande ugn (i praktiken en modifierad Sendzimiranordning) under vanliga betingelser. Den aluminium-; pläterade plåten utsattes för material- och oxidationsprovning. Re- sultaten (de mekaniska egenskaperna och oxidationsviktökningen) visas i samma tabell. Materialprovningen utfördes med prover som preparats enligt JIS (Japanese Industrial Standards) Z-2201, No. 5. skuren i valsningsriktningen, och oxídationsprovningen med fem upprepade turer av ett förlopp vid vilket proverna hålls vid 83006 i atmosfären i H8 h och kyles till rumstemperatur.After conventional pickling, the hot rolls were made of cold-rolled sheet metal with a thickness of 0.8 mm. The cold-rolled sheets thus prepared were heated at varying temperatures and plated with aluminum (60 g / m2) by means of a directly subsequent hot-plating device. of the annealing type with a non-oxidizing furnace (in practice a modified Sendzimir device) under normal conditions. The aluminum; the plated sheet was subjected to material and oxidation testing. The results (the mechanical properties and the oxidation weight increase) are shown in the same table. The material test was performed with samples prepared according to JIS (Japanese Industrial Standards) Z-2201, No. 5. cut in the rolling direction, and the oxidation test with five repetitions of a process in which the samples are kept at 83006 in the atmosphere for H8 h and cooled to room temperature.
I tabell 1 ligger proverna D, E och F inom det sammansättninge- intervall som definieras vid föreliggande uppfinning och F ligger inom ramen för föreliggande uppfinning i fråga om värmningstemperaturen före pläteringen. Denna tabell visar att material som är utmärkta både vad gäller formbarhet och oxidationsbeständighet endast uppnås då underlagsstålets sammansättning, upplindníngstemperaturen och pläte- ringstemperaturen tillfredsställer betingelserna definierade vid föreliggande uppfinning.In Table 1, samples D, E and F are within the composition range defined by the present invention and F is within the scope of the present invention in terms of the heating temperature before plating. This table shows that materials which are excellent in both formability and oxidation resistance are obtained only when the composition of the substrate steel, the winding temperature and the plating temperature satisfy the conditions defined by the present invention.
Vid jämförelse av prov A och B framgår att en minskning i Mn- halten bidrar till att sänka sträckgränsen. En jämförelse av B och C visar att även en tillsättning av Ti bidrar till att sänka sträckgrän- sen. En jämförelse av C och F visar att kombinerad tillsättning av Ti och Cr även bidrar till att sänka sträckgränsen.A comparison of samples A and B shows that a reduction in the Mn content contributes to lowering the yield strength. A comparison of B and C shows that the addition of Ti also contributes to lowering the yield strength. A comparison of C and F shows that the combined addition of Ti and Cr also helps to lower the yield strength.
J! 449 758 Tabell 2 visar de mekaniska egenskaperna hos de aluminiumplät- terade stålplåtsprover som iordningställdes genom åstadkommande av stålen med den sammansättning som anges däri och behandling av dem på samma sätt som ovan.J! 449 758 Table 2 shows the mechanical properties of the aluminum-plated steel sheet samples prepared by providing the steels with the composition specified therein and treating them in the same manner as above.
Av denna tabell framgår att Cr är effektivt för sänkning av sträckgränsen då det ingår i en mängd av ca 0,05-0,50 %.This table shows that Cr is effective for lowering the yield strength as it is included in an amount of about 0.05-0.50%.
Tabell 3 visar de mekaniska egenskaperna och oxidationsviktök- ningen hos de aluminiumpläterade stålplåtprover som iordníngstålldes genom åstadkommande av de stål vars sammansättning anges däri och behandling av dem på samma sätt som ovan. Av denna tabell framgår att då mängden tillsatt Ti är 0,1 % eller mer och mer än 10 ggr mängden C uppnås som effekt en sänkning av sträckgränsen och oxidationsvikt- ökningen. Som emellertid framgår av prov G ökar sträckgränsen igen då Ti-halten överskrider 0,5 %.Table 3 shows the mechanical properties and oxidation weight gain of the aluminum plated steel sheet samples prepared by producing the steels whose composition is stated therein and treating them in the same manner as above. This table shows that when the amount of Ti added is 0.1% or more and more than 10 times the amount of C, a reduction of the yield strength and the increase in oxidation weight is achieved as an effect. However, as can be seen from sample G, the yield strength increases again when the Ti content exceeds 0.5%.
Tabell 4-2 visar resultaten av samma provningar som ovan på prover som íordningställts på samma sätt som ovan av stål med den sam- mansättning som anges i tabell 4-1. Av denna tabell framgår att mate- rialet icke mjukgöres tillräckligt då upplindningstemperaturen är lägre än 700°C, men är anmärkningsvärd då värmningstemperaturen före plätering är 85000 eller högre.Table 4-2 shows the results of the same tests as above on samples prepared in the same way as above of steel with the composition given in Table 4-1. This table shows that the material is not softened sufficiently when the winding temperature is lower than 700 ° C, but is remarkable when the heating temperature before plating is 85000 or higher.
Föredragna utföringsformer av föreliggande uppfinning skall nu beskrivas närmare nedan.Preferred embodiments of the present invention will now be described in more detail below.
Exempel 1. De göt vars sammansättning anges i tabell 5 som prov nr 1 och nr 2 erhölls genom vakuumavgasning av smält stål fram- ställt i en LD-konverter i och för minskning av C och 0-halterna, och därefter genom justering av sammansättningen genom tillsättning av ferrolegeringar, t ex ferrokrom, ferrotitan, ferromangan; etc. Göten tillverkades somplatiner och dessa varmvalsades till 2,5 mm tjocka varma rullar under de i tabell 6 angivna betingelserna. Efter betning kallvalsades de varma rullarna till 0,8 mm tjock plåt. De kallvalsade plåtarna pläterades med aluminium medelst en direkt efterföljande varmpläteringsanordning av glödgningstyp med en icke-oxíderande ugn (en modifierad sendzimiranordning) under de i tabell 6 angivna be- tingelserna. De mekaniska egenskaperna och oxidationsviktökningen hos de sålunda erhållna aluminiumpläterade stålplåtarna som provades på samma sätt som ovan visas i tabell 6. Båda plåtarna uppvisade utmärka egenskaper - låg sträckgräns och hög oxidationsbeständighet vid höga temperaturer.Example 1. The ingots whose composition is given in Table 5 as Sample Nos. 1 and 2 were obtained by vacuum degassing of molten steel produced in an LD converter to reduce the C and O contents, and then by adjusting the composition by addition of ferroalloys, eg ferrochrome, ferrotitanium, ferromanganese; etc. The ingots were made as platinum and these were hot rolled into 2.5 mm thick hot rolls under the conditions given in Table 6. After pickling, the hot rolls were cold rolled into 0.8 mm thick sheet metal. The cold-rolled sheets were plated with aluminum by means of a directly subsequent hot-plating annealing-type plating apparatus with a non-oxidizing furnace (a modified sendzimir apparatus) under the conditions set forth in Table 6. The mechanical properties and the oxidation weight increase of the thus obtained aluminum-plated steel sheets tested in the same way as above are shown in Table 6. Both sheets exhibited excellent properties - low yield strength and high oxidation resistance at high temperatures.
Exempel 2. Platiner vars sammansättning anges i tabell 5 som nr 3 och U framställdes genom stränggjutning efter smältning på samma 449 758 s sätt som i exempel 1. Platinerna överfördes till aluminiumpläterad stålplåt på samma sätt som beskrivs i exempel 1. De mekaniska egen- skaperna och provningsresultaten av den sålunda erhållna stâlplâten som provades på samma sätt som i exempel 1 visas i tabell 6. Denna plåt har utmärkta egenskaper jämförbara med dem hos plåten 1 exempel 1.Example 2. Platinums whose composition is given in Table 5 as Nos. 3 and U were prepared by extrusion after melting in the same 449,758 s manner as in Example 1. The platinums were transferred to aluminum-plated steel sheet in the same manner as described in Example 1. The mechanical properties and the test results of the steel plate thus obtained which were tested in the same manner as in Example 1 are shown in Table 6. This plate has excellent properties comparable to those of the plate 1 Example 1.
Produkterna enligt föreliggande uppfinning lämpar sig för till- verkning av delar med komplicerad form för användning vid höga tempera- turer, t ex avgasbehandlingsapparater för förbränningsmotorer. 449 758 man: dö 3:5 2 mm C R 0% ON» âá 3.0 3.0 36 mäá m n n n n n awmflmnwusmw wa flm mfl fln øfiæ on» no o :H o ow o fifi o =oo o m h n n n n amwflmnmuaww ma wa mfi wm cmæ omm :Q o fifl c mm o MH o woo o Q n n a n |wwHmnmuEww æß flm mfi Hm omm oflß :Q o 1 Hm o mfl o »oo o o flmvw . « uwmflwuwwsww ænfi az mfl mm oææ omm =o.o 1 | mfi o woo o m n n n ammflmnmusww mmfi mr NN nm oßw oßm mo o 1 . 1 ww o »oo o < ANEEV Qv ^~ÉEå Neeäš Bov Sov É .G ä.. .š u wcwc wcmaw mcmnm 1.23. -VEWSW -finšm _ wcflcxæ Wucwuvßmfla _ ümwcflc |»xw> nmamxwcwww vfl> umemv wcfl: ^&v wcflcppwwcmñsmw xmflsmx >0nm |xumEc< umcoflu mxwficmxmä wcmuwfla |mHm>Enm> umvflxo wumwHm> uw> QEw» afifimx :mm lwwcflfiawmm H fifiwnwä 449 758 Hflßwwwfiwgwwsmä w: >H Nm mO.o wm.@ @fl.@ Hfi.Q =oo.Q w Mag: Hem Hwpw m= =« Nm n@.@ m=.o -.o =fi.Q ß0Q.@ m Qnuz Hem Hmpw flm zfi Hm m@.@ on.Q mfl.o nfi.O =@o.o m maa: Ham Hmßw Nm nfi Nm =o_Q mfi«o wfi.Q mfi.o moo.o Q ung: Hzw Hmßw Hm MH fln =o.o >°.Q o~.o >fi,O =Qo.o 0 Hmpmwwfiwnwwsww ww mfi fim mo.Q mono -_o mfi.o wo@“o m Hwumwmfiwfiwuemw Nq wfl Nm mo.o - mH.@ =fi.o ~@o.o < Awv ^@EE\@xV^~EE\@x, fi< po MB :E 0 mcwnw mcwnw nww=fi=x»we=< wcflcwwe 1x0m»»w |»»ø@m >0Lm nwmmxmcwmw mxmficmxmä ^wv wcficßpmwcmsmm xwflëmm N Hflwnwß 449 758 flwßwmwfiwhæueww mw H: :N mm nfl ofl.o wm.o ~HQ.o u una: Hmm Hmßw Nm m= ßfi mm »m ~fl.o =n.o @oo.@ m Man: Ham Hmum mn om =« Nm »M mH.o flN.o >oo.o m »mas Ham H«»m_ æ= mm mfi om om ««.o @«.o @oQ.o Q Hwuwwmflwpnwemh Nm w= ßfl mm flfi ~«.o wQ.o >oo.o U .wmas fiaw Hmum Hm ma wfi Nm fifi =fl.o m«.o Hfio.@ m Hw»m@mHwpm@swh¶ wflfi m= ma :N w fi«.o mfl.o @Ho.Q < ^Ne\wV ^«v ^~ee\@xv^~es\Qxv o\fle hu fia 0 wcwc mcmuw mcmuw nwmc«cxawE:< vwæa uxumuuw uuuonm >oAm wcflcxm IwuXHswwCOMuMUMXO .umflwåmflmww .mzmfifidxwí wCHGuummEMEEmw xwfiëmx n aamndfi 449 758 una: Hmm flmuw mn mm mfl om omm On» owm maa: Ham Hmpw ßz Nm mfi fim omm ON» omm Hwpwmwflwpmmaww wß m= mfi Nm ofim om» o=æ Hmpmmmflwnwweww fiofl m= »H nn omm Qmw omæ Hwßwwwflwnmueww mm q= wfl mm mom omm omæ 553 :S 655%: fsšaï 6% 8% 8% mcwnw mcmnw _ »news wnflcfiwe |xUwp»m |»»onm wcfiumßwfia @fl> -wwc«HQw~= »uemppsflw nmwc«:xnmE:< wcfi:xmmuxfi> Qëøu wcmamflm mv nmmfiwwcfluwn umcoflumufixo .Hwmmxwcmww mxwficmzm: .èmdmšflfimx :wa :wwfiucmflmkflënåw ~-= HHw@«a mm H~.o >No.o Ofi.Q @QQ.@ woo.0 ~H.o ~o.o @o0.O u\He wa H< nu m m az fiw Q fiuz Hflmnmë 449 758 11 =m flm nfi fin oww om* omm = mn mm nfi om omm owß o=w md m= fim Nfi om Oææ omß omæ NH w= om mfi flm Qom omß omm fin ^~s\wV ^Rv ^~es\@xv ^~ee\@xv Äøov ^o°V ^u0v .uaswu wcficwma wsmmwxummum mcmnwououm |mwcfiHummm uuëmuuzfim wcwnmuwflm mcficxm»xw> vfiëømëwu mcmumfia nwwfimwcfiuwn umcofiumwwxo nmmmxmcmww mxwwcmxw: mømwflw>HHmx :wa «mmcflcwHm>Euæ> >onm w Hflwßma fin -.o fl=@.o mo.o >oo.o woo.@ ~fi.o mo.Q ~oo.o :U mm o~.o wmo.o =H.o woQ.@ m@Q.o nfl.o =o.o woo.o mí mm fiN.@ =no.@ QH.o >oo.o woo.@ flfi.o m@.O @@O.@ N.The products according to the present invention are suitable for the manufacture of parts with a complicated shape for use at high temperatures, for example exhaust gas treatment apparatus for internal combustion engines. 449 758 man: dö 3: 5 2 mm CR 0% ON »âá 3.0 3.0 36 mäá mnnnnn awm fl mnwusmw wa fl m m fl fl n ø fi æ on» no o: H o ow o fifi o = oo omhnnnn amw fl mnmuaww ma wa m fi wm cmæ omm: Q o fifl c mm o MH o woo o Q nnan | wwHmnmuEww æß fl m m fi Hm omm o fl ß: Q o 1 Hm o m fl o »oo oo fl mvw. «Uwm fl wuwwsww æn fi az m fl mm oææ omm = o.o 1 | m fi o woo o m n n n amm fl mnmusww mm fi mr NN nm oßw oßm mo o 1. 1 ww o »oo o <ANEEV Qv ^ ~ ÉEå Neeäš Bov Sov É .G ä .. .š u wcwc wcmaw mcmnm 1.23. -VEWSW -fi NSM _ wc al cxæ Wucwuvßm al A _ ümwc f c | "xw> nmamxwcwww v fl> umemv toilet fl ^ & v toilet al cppwwcmñsmw microns al SMX> 0nm | Xumec <UMCO fl u mxw fi cmxmä wcmuw f a | MHM> ENM> UMV al xo wumwHm> uw> QEW» A fifi mx: mm lwwc flfi awmm H fifi wnwä 449 758 H fl ßwww fi wgwwsmä w:> H Nm mO.o wm. @ @ Fl. @ H fi. Q = oo.Q w Mag: Hem Hwpw m = = «Nm n @. @ M = .o -.o = fi. Q ß0Q . @ m Qnuz Hem Hmpw fl m z fi Hm m @. @ on.Q m fl. o n fi. O = @ oo m maa: Ham Hmßw Nm n fi Nm = o_Q m fi «o w fi. Q m fi. o moo.o Q ung: Hzw Hmßw Hm MH fl n = oo> ° .Q o ~ .o> fi, O = Qo.o 0 Hmpmww fi wnwwsww ww m fi fi m mo.Q mono -_o m fi. O wo @ “om Hwumwm fi w fi wuemw Nq w fl Nm mo.o - mm. . @ = fi. o ~ @ oo <Awv ^ @ EE \ @ xV ^ ~ EE \ @x, fi <po MB: E 0 mcwnw mcwnw nww = fi = x »we = <wc fl cwwe 1x0m» »w |» » ø @ m> 0Lm nwmmxmcwmw mxm fi cmxmä ^ wv wc fi cßpmwcmsmm xw fl ëmm N H fl wnwß 449 758 fl wßwmw fi whæueww mw H:: N mm n fl o fl. o wm.o ~ HQ.m m. @ oo. @ m Man: Ham Hmum mn om = «Nm» M mH.o fl N.o> oo.om »mas Ham H« »m_ æ = mm m fi om om« «.o @«. o @oQ. o Q Hwuwwm fl wpnwemh Nm w = ß fl mm flfi ~ «.o wQ.o> oo.o U .wmas fi aw Hmum Hm ma w fi Nm fifi = fl. om« .o H fi o. @ m Hw »m @ mHwpm @ swh¶ w flfi m = ma: N w fi«. o m fl. o @ Ho.Q <^ Ne \ wV ^ «v ^ ~ ee \ @ xv ^ ~ es \ Qxv o \ fl e hu f a 0 wcwc mcmuw mcmuw nwmc «cxawE: <vwæa uxumuuw uuuonm> OAM toilet al CXM IwuXHswwCOMuMUMXO .um al WAM al MWW .mzm fifi dxwí wCHGuummEMEEmw xw fi EMX n aamnd fi 449,758 una: Hmm al MUW mn mm others on iff on» owm MAA: Ham Hmpw SSZ Nm m f f m if and only if oN » omm Hwpwmw fl wpmmaww wß m = m fi Nm o fi m om »o = æ Hmpmmm fl wnwweww fi o fl m =» H nn omm Qmw omæ Hwßwww fl wnmueww mm q = w fl mm mom omm omæ 553: S 655% mw 8w mn. wn f c f we | xUwp »m |» »onm wc f umßw FI A @ fl> -wwc« HQw ~ = »uempps al w NMWC«: xnmE: <wc f: xmmux fi> Qëøu wcmam fl m mv NMM fi wwc al uwn UMCO al umu f xo .Hwmmxwcmww mxw fi cmzm: .èmdmš flfi mx: WA: ww fi ucm al mk al ënåw ~ - = HHW @ «A mm H ~ .o> No.o O fi. Q @ QQ. @ Woo.0 ~ Ho ~ oo @ o0.O u \ He wa H <nu mm az fi w Q fi uz H fl mnmë 449 758 11 = m fl m n fi fi n oww om * omm = mn mm n fi om omm owß o = w md m = fi m N fi om Oææ omß omæ NH w = om m fi fl m Qom omß omm fi n ^ ~ s \ wV ^ Rv ^ ~ es \ @xv ^ ~ ee \ @xv Äøov ^ o ° V ^ u0v .uaswu wc fi cwma wsmmwxummum mcmnwououm | mwc fi Hummm uuëmuuz fi m wcwnmuw fl m mc fi cxm »xw> v fi ëømëwu mc mum fi a nww fi mwc fi uwn umco fi umwwxo nmmmxmcmww mxwwcmxw: mømw fl w> HHmx: wa «mmc fl cwHm> Euæ>> onm w H fl wßma fi n -.o fl = @. o mo.o> oo.o woo. : U mm o ~ .o wmo.o = Ho woQ. @ M @ Qo n fl. O = oo woo.o mí mm fi N. @ = no. @ QH.o> oo.o woo. @ Flfi. Om @. O @@ O. @ N.
NN mH_Q wNo.o fi«.o moo.o moO.o ~fi.o ~@.o >o@.@ fih u\fis fia H< ho w m cs Mm U fifiv wsflcuummcmsëmm xmwemx >onm m HfimnmëNN mH_Q wNo.o fi «. O moo.o moO.o ~ fi. O ~ @ .o> o @. @ Fi h u \ fi s fi a H <ho w m cs Mm U fifi v ws fl cuummcmsëmm xmwemx> onm m H fi mnmë
Claims (1)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP533380A JPS56102523A (en) | 1980-01-22 | 1980-01-22 | Manufacture of aluminum-plated steel sheet having resistance to oxidation at high temperature |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| SE8100310L SE8100310L (en) | 1981-07-23 |
| SE449758B true SE449758B (en) | 1987-05-18 |
Family
ID=11608303
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| SE8100310A SE449758B (en) | 1980-01-22 | 1981-01-20 | PROCEDURE FOR MANUFACTURING MELTALUMINUM PLATED STEEL PLATE |
Country Status (15)
| Country | Link |
|---|---|
| JP (1) | JPS56102523A (en) |
| AU (1) | AU538073B2 (en) |
| BE (1) | BE887191A (en) |
| BR (1) | BR8100316A (en) |
| CA (1) | CA1178182A (en) |
| DE (1) | DE3101850C2 (en) |
| DK (1) | DK157690C (en) |
| ES (1) | ES8204477A1 (en) |
| FR (1) | FR2474060A1 (en) |
| GB (1) | GB2069001B (en) |
| IT (1) | IT1143260B (en) |
| NL (1) | NL182414C (en) |
| NZ (1) | NZ196063A (en) |
| SE (1) | SE449758B (en) |
| ZA (1) | ZA8167B (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6013053A (en) * | 1983-07-04 | 1985-01-23 | Nisshin Steel Co Ltd | Aluminized steel sheet with superior strength at high temperature and superior heat resistance |
| JPS6043476A (en) * | 1983-08-17 | 1985-03-08 | Nippon Steel Corp | Continuous aluminizing method |
| JPS61177378A (en) * | 1985-02-01 | 1986-08-09 | Nippon Steel Corp | Chromated cr-containing steel sheet having superior suitability to coating with paint |
| US8453482B2 (en) * | 2008-04-22 | 2013-06-04 | Nippon Steel & Sumitomo Metal Corporation | Plated steel sheet and method of hot-stamping plated steel sheet |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CA1015231A (en) * | 1971-12-07 | 1977-08-09 | David W. Gomersall | Aluminum coated steel |
| US3881880A (en) * | 1971-12-07 | 1975-05-06 | Inland Steel Co | Aluminum coated steel |
| DE2264519A1 (en) * | 1972-11-13 | 1974-05-22 | Toyo Kogyo Co | Aluminising treatment for automobile mufflers - improve high temp. corro-sion resistance as well as giving oxidn. resistance |
| US3881882A (en) * | 1973-04-19 | 1975-05-06 | Inland Steel Co | Aluminum coated steel |
| US3905780A (en) * | 1973-06-25 | 1975-09-16 | Armco Steel Corp | Oxidation-resistant low alloy steel with Al coating |
| JPS5135532A (en) * | 1974-09-20 | 1976-03-26 | Sumitomo Shipbuild Machinery | KAATSUSENKANSHI KISAIDEIHO |
| JPS582248B2 (en) * | 1976-09-16 | 1983-01-14 | 日新製鋼株式会社 | Manufacturing method for hot-dip galvanized steel sheet with excellent workability |
| US4144379A (en) * | 1977-09-02 | 1979-03-13 | Inland Steel Company | Drawing quality hot-dip coated steel strip |
-
1980
- 1980-01-22 JP JP533380A patent/JPS56102523A/en active Granted
-
1981
- 1981-01-06 ZA ZA00810067A patent/ZA8167B/en unknown
- 1981-01-07 NL NLAANVRAGE8100030,A patent/NL182414C/en not_active IP Right Cessation
- 1981-01-09 IT IT67019/81A patent/IT1143260B/en active
- 1981-01-16 AU AU66291/81A patent/AU538073B2/en not_active Ceased
- 1981-01-19 DK DK022381A patent/DK157690C/en active
- 1981-01-20 SE SE8100310A patent/SE449758B/en not_active IP Right Cessation
- 1981-01-20 FR FR8100958A patent/FR2474060A1/en active Granted
- 1981-01-20 CA CA000368870A patent/CA1178182A/en not_active Expired
- 1981-01-21 NZ NZ196063A patent/NZ196063A/en unknown
- 1981-01-21 DE DE3101850A patent/DE3101850C2/en not_active Expired
- 1981-01-21 BR BR8100316A patent/BR8100316A/en unknown
- 1981-01-21 GB GB8101817A patent/GB2069001B/en not_active Expired
- 1981-01-22 ES ES498742A patent/ES8204477A1/en not_active Expired
- 1981-01-22 BE BE0/203568A patent/BE887191A/en not_active IP Right Cessation
Also Published As
| Publication number | Publication date |
|---|---|
| BE887191A (en) | 1981-07-22 |
| ES498742A0 (en) | 1982-05-01 |
| DK157690C (en) | 1990-07-02 |
| DE3101850C2 (en) | 1983-12-22 |
| JPS633929B2 (en) | 1988-01-26 |
| IT8167019A0 (en) | 1981-01-09 |
| GB2069001B (en) | 1983-06-02 |
| IT1143260B (en) | 1986-10-22 |
| NL8100030A (en) | 1981-08-17 |
| ZA8167B (en) | 1982-03-31 |
| JPS56102523A (en) | 1981-08-17 |
| AU6629181A (en) | 1981-07-30 |
| CA1178182A (en) | 1984-11-20 |
| DK22381A (en) | 1981-07-23 |
| FR2474060A1 (en) | 1981-07-24 |
| SE8100310L (en) | 1981-07-23 |
| NL182414C (en) | 1988-03-01 |
| AU538073B2 (en) | 1984-07-26 |
| NZ196063A (en) | 1984-02-03 |
| BR8100316A (en) | 1981-08-11 |
| DK157690B (en) | 1990-02-05 |
| GB2069001A (en) | 1981-08-19 |
| ES8204477A1 (en) | 1982-05-01 |
| DE3101850A1 (en) | 1981-11-19 |
| NL182414B (en) | 1987-10-01 |
| FR2474060B1 (en) | 1984-06-01 |
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