DE102005023952B9 - Security armor for protection against fire and methods of manufacture - Google Patents

Abstract

safety armor for protection against fire, comprising a shield (1) made of an alloyed steel consisting of a base carbon content of less than 0.3% by mass and by a thermochemical Treatment in one of at least one top surface (D1) of the shield (1) outgoing Edge zone (R) with strength-increasing Enriched elements, such as carbon and / or nitrogen, the steel as a result of after the thermochemical treatment conducted thermal treatment, such as hardening and / or tempering, a increased Has surface hardness, characterized in that the steel in the edge zone (R) on at least 0.5% by mass carbon enriched and on the top surface (D1) in the presence of carbides has a minimum hardness of 55 HRC, wherein the shield (D1) with a bullet resistance according to the classes B3 and higher according to the DIN standards EN 1522 and DIN EN 1523 both in the carbon-enriched Edge zone (R), as well as in a little or no carbon Enriched area (B) comparatively lesser ...

Description

The Invention relates to a safety armor for protection against fire, comprising a shield, which consists of an alloyed steel, having a base carbon content of less than 0.3 mass% of carbon possesses and by a thermochemical treatment in one of at least a top surface of the shield emanating edge zone with strengthening elements, such as carbon and / or nitrogen, is enriched, wherein the Steel as a result of a thermal treatment carried out after the thermochemical treatment Treatment, such as hardening and / or tempering, an increased Has surface hardness. Furthermore, the invention relates to a method for the production such armor.

For armor of vehicles or other objects, such as security containers are known security armor consisting of fully hardened steels, hard manganese steels with manganese contents of 12 to 14 percent by mass (wt .-%) with simultaneous carbon contents of 1.2 Ma .-% to 1.4 Ma .-% or of plated, in particular roll-plated, steels exist. Examples of such standard market steels, the materials Ultrafort (stainless steel Witten-Krefeld, material number Fa.: 1.6355), for example, 6355, Thyrodur ^® X and Z (from stainless steel Witten-Krefeld, material numbers. 1.27XX) Dipro 50 and 60 M (Fa Dillinger Hütte GTS) and Secure 500 (Thyssen Krupp Stahl AG) among others.

armor materials are usually in terms of their safety characteristics subjected to a so-called bombardment test, being in Germany at present, in particular, the standards DIN EN 1522, Edition: 1999-02 "Windows, doors, shutters - Bullet resistance - Requirements and classification "; German Version EN 1522: 1998 and DIN EN 1523, Ausgabe: 1999-02 "Windows, doors, shutters - Bullet resistance - Test methods"; German version EN 1523: 1998 are binding. Besides, these materials can also according to a safety standard valid in a certain country - or also unclassified - tested using other than the standard weapons provided be, for. In Russia the Kalashnikov.

The bullet resistance is given in classes according to the following table.

To achieve a high firing class, it is necessary that the materials used on the one hand have a high surface hardness to deflect or destroy the ball, and on the other hand sufficiently tough to consume the kinetic energy of the projectile without cracking.

A safety armor of the type mentioned is from the RU 2 090 828 C1 known. This document describes a steel armor which is to be used in protective vests or shields and which, in contrast to the steels described above as commercially available, consists of a steel obtained by a thermochemical treatment in an edge zone with strength-increasing elements as described, in particular enriched with carbon. According to the patent, a special steel grade with the following composition is used: C - 0.20 to 0.27 mass%, Si - 1.20 to 1.50 mass%, Mn - 0.3 to 0.90 mass. -%, Ni - 0.50 to 1.20 wt%, Cr - 1.10 to 1.50 wt%, Mo 0.15 to 0.35 wt%, Fe - residue. It becomes It is particularly emphasized that the required high hardness is achieved by the alloy with silicon (Si) and the required high toughness by the alloy with nickel (Ni). A disadvantage of the method of manufacturing the known safety armor but are the energy-consuming high austenitizing temperature, which is 920 ° C for the described material, and a precisely observed heating rate of 1.5 to 2.5 ° C / s in the thermal treatment, since in the opposite case, sets a ferritic-bainitic structure which no longer guarantees the safety characteristics desired for the armor.

Of the Invention is based on the object, a security armor of the type mentioned and a method for their preparation to be created by the warranty the desired safety characteristics for the armor, in particular bullet resistance according to the classes B3 and higher according to the standards DIN EN 1522 and DIN EN 1523, a reduction of the effort and a greater freedom in the technological leadership of the manufacturing process can be achieved.

These Task is solved by that the steel in the edge zone to at least 0.5 mass% of carbon enriched - or Enriched according to the method will - and in the presence - or according to the proceedings Training - from Carbides on the top surface a minimum hardness of 55 HRC, which according to the method by the thermal treatment is set, with the shield, both in the carbon enriched edge zone, as well as in a little or no carbon enriched area comparatively lesser Hardness one Has a content of silicon of not more than 0.4% by mass.

The Invention is based on a from various investigations Inferring that an alloy with silicon and with Nickel for the production of security armor in the firing classes B3 to B7 as well as for the production of a safety with shelling with military Caliber not only is not necessary, but that even through the suppression of the influence of silicon as an alloying element on the one hand the necessary austenitizing temperature for a thermochemical or thermal treatment are lowered and on the other hand, a carbon accumulation in a much wider than that known in the art Area, for example, an overcooling, can be made. This is in the presence of silicon above the content of 0.4% by weight not possible because the silicon on the one hand ausschnit the austenite of the iron and the stability from the invention in the structure of the steel formed, especially secondary, Iron carbides degrades to decomposition under graphitization.

a Particularly preferred material according to the invention is under These points of view represent a steel, the following values of the chemical Melt Analysis: C - 0.17 to 0.20% by mass, Si - 0.20 to 0.30 mass%, Mn - 1.15 up to 1.30 mass%, P - maximum 0.030% by mass, S - maximum 0.030% by weight, Al - 0.020 to 0.050 mass%, Cu - maximum 0.25 mass%, Ni - maximum 0.25 mass%, Cr - 1.15 to 1.30 mass%, Ti - 0.02 to 0.05 mass%, B - 0.0015 to 0.004% by mass. This steel is a case-hardening steel, which is known under the material designation 1.7160 or 16 MnCr 5 BP and is in trade.

This base material is adjusted by the thermochemical treatment and the heat treatment to the required ballistic properties. In this case, a carburization may take place as the thermochemical treatment, whereby it is achieved that either a hypoeutectoid or preferably a hypereutectoid carbon content in the range of at least 0.5 mass%, particularly preferably 1.1 mass%, is present on the bombardment side. Depending on the composition of the steel, formation of carbides-either of, for example, especially secondary-formed cementite (Fe ₃ C) and / or of special carbides, such as, for example, (Cr, Fe) ₇ C ₃ , is reached.

On the side opposite the bombardment side, it is likewise possible to set a carbon content of 0.5% by mass to 3.5% by mass, with or without the formation of carbides, the carbon content of the two opposite sides being the same or different , That's what makes it that the sign of both top surfaces emanating, carbon-enriched edge zones comparatively higher hardness, each having the same or different carbon content and each having the same or different hardness, which with decreasing carbon content lying in the between the edge zones not or only slightly enriched with carbon region comparatively lower hardness pass.

It can be provided in particular that according to a each selected Depth (depth of hardening) the carbon enriched edge zone (s) after hardening and a tempering of the thermochemically treated steel at most about 50%, preferably at most about 1/3, the thickness of the thickness of the shield is substantially the original one Hardness of Steel or slightly higher Have hardness and at least about 50%, preferably at least about 2/3, of the thickness the shield a higher Have hardness.

at Presence of two edge zones can match these - adapted to the threat class - with different ones hardening depths and carbon contents. The purpose of this technical measure is thereby, on the shelling side by a comparatively higher Einhärtungstiefe and strong carbide enrichment to destroy impacting hard-core ammunition break up and on the back the exit of the projectile through an elastic and hard edge zone to prevent. Furthermore is also the splitting or splintering of sharp-edged steel parts prevents, whereby a possibly existing additional Tissue protection (backing) is saved from being cut.

Besides that is it also possible that the shield in the area of the top surfaces only partially thermochemical is treated.

Around the desired To achieve properties, carburizing can be one or more times respectively. Another possibility is also that the thermochemical treatment as a Carbonitration carried out becomes, making it near the surface next to a carbide formation also leads to nitride formation, which in the sense the invention is also considered to be advantageous.

With a multiple carburization at different carburizing temperatures the formation of the carbides can be influenced in such a way that on at least one side a graded layer of fine and coarse Carbides formed with more or less heavily occupied grain boundary. Hereby, the mentioned destruction capability the border zone for Projectiles are set.

By the thermal treatment, which initially involves curing, by means of which the maximum hardness in the edge by single or double hardening and toughness is set in the core, a desired hardness, in particular of at least 55 HRC, preferably more than 60, more preferably 64 HRC to 67 HRC.

to Achieving a good flatness of the surface of the shield can hardening in particular in a quette, i. under forced and pressurized pressure. In terms of process engineering, this also has an advantageous effect, that an elevated hydrostatic pressure lowers the austenitizing temperature. For final adjustment the hardness and tenacity - both in the carbon-enriched edge zone as well as in the not or only slightly enriched with carbon area comparatively lower hardness - can after the hardening preferably a tempering be made.

Next It is also the steel mentioned above as being particularly preferred possible, that the steel used is a low or high alloyed, Chromium, in particular chromium together with manganese and / or molybdenum containing Steel, such as 25 CrMo 4, 17 CrNiMo6, 13 CrMo 4 5, 20 MnCr5 or X 19 NiCrMo 4, is.

The Presence of chromium in the for these steels characteristic amount lowers the austenitizing temperature, favored carbide formation lowers the critical cooling rate during curing and increases hardenability. The content of chromium in the steel should not be greater as about 1.6% by mass, and preferably in the range of 1.15% by mass to 1.30% by weight.

The presence of molybdenum enhances hardenability and reduces temper embrittlement. The preferred molybdenum contents are in the range of 0.20% by weight to 0.40% by weight. Furthermore, the molybdenum has the ability to inventively provided carbides (MoC, MoC ₂ , mixed carbides with iron). Molybdenum also has an advantageous effect on increasing the penetration depth of the Carbon in the thermochemical treatment and thus leads to an increase in the carbon content in the peripheral zone.

In In this context, it should be noted that this is also the presence of nickel - though not as essential according to the invention considered - in an amount of more than one wt .-% not according to the invention is excluded and therefore the steel is also a high alloyed, in particular Nickel-containing steel, such as the aforementioned X 19 NiCrMo 4, can be.

When very cheap It is within the scope of the invention, when the steel is a low-alloyed, predominantly Manganese-containing steel, such as 16 MnCr 5, 16 MnCrS 5, 20 MnCr 5, 21 MnCr or 20 MnCrS 5, is. The presence of manganese in the for this steels characteristic amount lowers the austenitizing temperature as well the critical cooling rate while hardening and increased the hardenability. Furthermore Manganese forms manganese sulphides, which have a harmful effect of sulfur compensate. Therefore, too higher Sulfur concentrations in the material may be present than those for the above as particularly preferred steel. Because manganese is the Carbon activity raised in the iron, is a decomposition of iron carbides - in contrast to the ratios at the presence of silicon - inhibited. Manganese is known to work also as a deoxidizer. The content of manganese in the steel should according to the invention in particular greater than about 0.8 mass%, preferably greater than 1.0 mass% but less than about 2.5 mass%, preferably smaller than 2.0 wt%, and more preferably in the range of 1.15 % By weight to 1.30% by mass.

To to a carbon content of about 1.6 wt .-% is these manganese steels thus to so-called pearlitic manganese steels, so not to the known to Manufacture of security armor Hartmanganstähle used, the a much higher one Have manganese content. However, it is in the present invention taking place Carbon enrichment, which also up to a carburization unusually high Lead carbon contents can, but possible, that in the marginal zone of the shield first an austenitic microstructure education which is similar to that found in manganese hard steels.

The Shield of the security armor may in particular be plate-shaped, i. with at least two, in particular substantially parallel to each other running, cover surfaces, the larger compared to existing edge surfaces a larger size have, be formed. The plate size (length and width) depends according to the particular application and arises in terms their maximum dimensioning from the technological conditions in the processing of sheets. The shield should preferably have a minimum thickness of about 3.0 mm; a maximum thickness should be in the range from about 10.0 mm to 25.0 mm.

It may advantageously be provided that in the security armor according to the invention the shield is connected to a, in particular high-strength, impact-resistant, tear-resistant, chemically resistant flame-retardant and / or self-extinguishing support, such as a protective fabric consisting of para-aramid fibers. Such protective ^{fabrics are} known, for example, under the name ^Kevlar® .

In the dependent claims and in the following description are further advantageous versions of the invention.

in the The following will illustrate the invention by way of example with reference to FIG closer to the enclosed drawing explained. Show it:

1 a cross section through a safety armor according to the invention for protection against fire,

2 a greatly enlarged section of a characteristic of a security armor structure according to the invention.

As in 1 illustrated, a security armor according to the invention for protection against bombardment comprises a shield 1 , This sign 1 consists of an alloyed steel having a base carbon content of less than 0.3 mass% of carbon, which in the diagram contained in the figure, which shows the course of the concentration of carbon (C) over the cross section (thickness d) of the shield 1 shows, is indicated schematically by lying in the right part of the curve section. The corresponding area of the shield is designated by the reference symbol B. The carbon content is thus in a concentration range, as it is characteristic of case-hardening steels.

Of the Steel has the following values of chemical melting analysis: C - 0.17 to 0.20% by mass, Si - 0.20 to 0.30 mass%, Mn - 1.15 up to 1.30 mass%, P - maximum 0.030% by mass, S - maximum 0.030% by weight, Al - 0.020 to 0.050 mass%, Cu - maximum 0.25 mass%, Ni - maximum 0.25 mass%, Cr - 1.15 to 1.30 mass%, Ti - 0.02 to 0.05 mass%, B - 0.0015 to 0.004% by mass.

By a thermochemical treatment is in one of the top surface D1 of the shield 1 representing the bombardment side, outgoing edge zone R of the steel with strengthening elements, enriched with carbon, which is indicated diagrammatically by the curve section in the left part of the diagram. The shield 1 is thus carburized in the boundary zone R for carbon accumulation, in particular overcooled.

The Thermochemical treatment for carburizing can at a temperature in the range between 900 ° C and 1040 ° C and with a treatment duration in the range of 30 to 720 minutes, especially with a gaseous Medium, such as in a propane-enriched endogas atmosphere or in low pressure with ethane, carried out become. Optionally, by repeated repetition of the thermochemical Treatment, in the peripheral zone R of the carbon to a concentration of at least 0.8% by mass, in particular more than 1.1% by mass to to 3.5 wt .-%, to be enriched.

As a result of a thermal treatment, such as hardening and / or tempering, carried out after the thermochemical treatment, the steel on the top surface D1 has an increased surface hardness determined by the Rockwell method (Rockwell C). In particular, it will have a hardness in the range of about 60 to 67 HRC on the top surface D1 of the sign 1 set.

The thermal treatment includes Austenitization, preferably at a temperature in the range from 800 ° C up to 880 ° C, followed by deterrence, especially with oil. The deterrent is preferably done in a quette, i. under pressure and pressurization.

The Austenitization and quenching can be carried out as required as a double cure, where in a first curing process the Austenitisierungstemperatur on the not or only slightly with Carbon enriched area B of the steel and in a second curing, the austenitizing temperature on the carbon-enriched Area R of the steel is tuned. This creates very fine needle Martensite as a hardened structure and through the starting effect Also, a grain refinement in which is little carbon enriched area B reached.

The thermal treatment following the thermochemical treatment comprises tempering, in particular with a tempering time in the range of up to 3 hours at a temperature in the range of up to 300 ° C. The hardness in the not or only slightly carburized area B of the sign 1 in particular may be in the range of about 35 to 47 HRC thereafter.

The graphic representation in 1 It should also be noted that, according to a selected depth t, of the carbon-enriched edge zone R after hardening and tempering of the steel is less than 50% of the thickness D of the shield 1 have substantially the original hardness of the steel or a slightly higher hardness and at least about 50% of the thickness D of the shield 1 have a higher hardness. This thickness D of the shield 1 may in particular be in the range of about 3.0 mm to 10 mm, for example 7.5 mm.

As further out 1 it is apparent in the illustrated embodiment of the invention that the shield 1 with a, in particular high-strength, impact-resistant, tear-resistant, chemically resistant flame-retardant and / or self-extinguishing, edition 2 , as with a protective fabric consisting of para-aramid fibers, which is located in particular on the side facing away from the bombardment.

In the 2 shown obtained from an electron micrograph section of the structure G on the top surface D1 of the carbon-enriched edge zone R shows that typical for a security armor according to the invention structure G comprises a matrix M of a tempered mixed structure, which martensite and a small proportion of retained austenite and / or interstitial structure such as bainite. Furthermore, it can be seen that the carbon-enriched edge zone - preferably spherical and lamellar - embedding E in the structure G, which chemically as nitrides or carbides, especially as secondary iron carbides or as special carbides, such as mixed carbides of Chromium and / or molybdenum, and in addition to the martensite are responsible for the high surface hardness of the top surface D1.

A determination of the firing properties of the safety armor according to the invention according to the standards DIN EN 1522 and DIN EN 1523 showed that the shield 1 (without fabric pad 2 ) in any case had a bullet resistance corresponding to the classes B3 and higher, with a higher carbon content, the double hardness and quenching in the Quette tended to assign the respective larger class values and both the bullet class B7 and a bulletproof was achieved when using military caliber.

The invention is not limited to the illustrated embodiment, but also includes all the same in the context of the invention embodiments. It has already been pointed out in this regard that the steel composition of the shield 1 may differ from the exemplified melt analysis.

In this connection, it is emphasized that the use of an alloyed steel having a basic carbon content of less than 0,3% by mass of carbon and a maximum content of silicon of 0.4% by mass and by a thermochemical treatment in one Enriched edge zone with strength-enhancing elements, such as carbon and / or nitrogen, as a material for producing a security armor for protection against bombardment, which in particular can be produced according to the method described above, is attributed inventive significance. Other rules that describe the particularly advantageous for the alloy compositions for the shield 1 , as the content of manganese, chromium, molybdenum and nickel, have been mentioned above.

Furthermore, the person skilled in the art can also provide other expedient features or technical measures for constructive design of the safety armor according to the invention. It has already been mentioned that the shield 1 from its two top surfaces D1, D2 outgoing, enriched with carbon edge zones R may have comparatively higher hardness, in each of which the same or a different carbon content and, accordingly, each may have the same or a different hardness. The area B of comparatively lower hardness which is not enriched with carbon, or only slightly enriched with carbon, would then lie between these two edge zones R located under the cover surfaces D1, D2.

It is also within the scope of the invention, when the two top surfaces D1, D2 of the shield 1 the security armor according to the invention not parallel, but slightly oblique to each other, which under certain circumstances improved bullet defense can be achieved.

Further the invention is not limited to those in independent claims 1, 22 and 33 defined combinations of features limited, but can also be through any other combination of certain characteristics be defined all of the individual characteristics disclosed. This means that basically practical omitted or by individual feature of the claims at least one individual feature disclosed elsewhere in the application can be replaced. Inso far the claims are only as a first Formulation trial for to understand an invention.

1

sign

2

Edition on 1

B

not carburized area of 1 lower hardness

D

Thickness of 1

d

Thickness of 1 , Variable in the diagram

D1

Deck area of 1 , Shelling site

D2

Deck area of 1 , Facing D1

e

embedding in G

G

Structure of 1 in R (on D1)

M

matrix from G

R

carburized edge zone of 1 higher hardness

t

depth from R

Claims (41)

Security armor for protection against fire, comprising a shield ( 1 ), which consists of an alloyed steel having a basic carbon content of less than 0.3 mass% and by a thermochemical treatment in one of at least one top surface (D1) of the shield ( 1 ) is enriched with strengthening elements such as carbon and / or nitrogen, wherein the steel has an increased surface hardness as a result of a thermal treatment carried out after the thermochemical treatment, such as hardening and / or tempering, characterized in that the steel in the edge zone (R) is enriched to at least 0.5 mass% of carbon and has a minimum hardness of 55 HRC on the top surface (D1) in the presence of carbides, the shield (D1) with a bullet resistance corresponding to the classes B3 and higher in accordance with the standards DIN EN 1522 and DIN EN 1523 both in the carbon-enriched edge zone (R) and in a region (B) of relatively low hardness which is not or only slightly enriched with carbon, a maximum silicon content of 0, 4% by mass. Security armor according to claim 1, characterized in that the shield ( 1 ), from both top surfaces (D1, D2) outgoing, carbon-enriched edge zones (R) comparatively higher hardness, each having the same or different carbon content and each having the same or different hardness, which with decreasing carbon content in the lying between the edge zones not or only slightly with Carbon-enriched area (B) relatively lower hardness transition. Security armor according to claim 1 or 2, characterized in that the shield ( 1 ) is carburized in the edge zone (s) (R) for carbon enrichment, in particular over carbonized. Security armor according to claim 1 or 2, characterized in that the shield ( 1 ) is carbonitrided in the edge zone (s) (R) for carbon enrichment. Security armor according to one of claims 1 to 4, characterized in that the steel is a low or high alloy, Chromium, in particular chromium together with manganese and / or molybdenum containing Steel, such as 25 CrMo 4, 17 CrNiMo6, 13 CrMo 4 5, 16 MnCr 5 BP, 20 MnCr5 or X19 NiCrMo4, is. Security armor according to one of claims 1 to 5, characterized in that the steel is a low-alloy, predominantly manganese-containing steel, such as 16 MnCr 5, 16 MnCr 5 BP, 16 MnCrS 5, 20 MnCr 5, 21 MnCr 5 or 20 MnCrS 5. Security armor according to one of claims 1 to 6, characterized in that the content of manganese in the steel greater than about 0.8 mass%, preferably greater than 1.0 mass% but less than about 2.5 mass%, preferably smaller is 2.0 wt%, with the content of manganese being particularly preferred in the range of 1.15% by weight to 1.30% by weight. Security armor according to one of claims 1 to 7, characterized in that the content of chromium in the steel is not is larger than about 1.6 mass%, and preferably in the range of 1.15 mass% to 1.30 mass% lies. Security armor according to one of claims 1 to 8, characterized in that the steel has the following chemical values Melt Analysis: C - 0.17 to 0.20% by mass, Si - 0.20 to 0.30 mass%, Mn - 1.15 up to 1.30 mass%, P - maximum 0.030% by mass, S - maximum 0.030% by weight, Al - 0.020 to 0.050 mass%, Cu - maximum 0.25 mass%, Ni - maximum 0.25 mass%, Cr - 1.15 to 1.30 mass%, Ti - 0.02 to 0.05 mass%, B - 0.0015 to 0.004% by mass. Security armor according to one of claims 1 to 5, characterized in that the steel is a high-alloy, in particular Nickel-containing steel such as X 19 NiCrMo 4. Security armor according to one of claims 1 to 10, characterized in that the steel in the edge zone (s) (R) to at least 0.8 mass%, in particular to more than 1.1 mass% up to 3.5% by weight, carbon-enriched. Security armor according to one of claims 1 to 11, characterized in that the steel in the edge zone (s) a hardness of more than 60 HRC, in particular in the range of 64 to 67 HRC. A security armor according to any one of claims 1 to 12, characterized in that according to a respective selected depth (t) of the carbon-enriched edge zone (s) after hardening and annealing of the thermochemically treated steel at most about 50% of the thickness (D. ) of the shield ( 1 ) have substantially the original hardness of the steel or a slightly higher hardness and at least about 50% of the thickness (D) of the shield ( 1 ) have a higher hardness. Safety armor according to one of claims 1 to 13, characterized in that corresponding to a respectively selected depth (t) of the carbon enriched edge zones (R) after hardening and tempering of the thermochemically treated steel at most about 1/3 of the thickness (D) of Shields ( 1 ) has substantially the original hardness of the steel or a slightly higher hardness and at least about 2/3 of the thickness (D) of the shield ( 1 ) have a higher hardness. Security armor according to one of claims 1 to 14, characterized in that the carbon-enriched (s) Edge zone (s) (R) comprises a matrix (M) of a structure (G), which martensite and a small proportion of retained austenite and / or interstitial structure, such as Bainite, contains. Security armor according to one of claims 1 to 15, characterized in that the carbon-enriched (s) Randzone (s) (R) as carbides, especially secondarily formed, iron and optionally Special carbides, such as mixed carbides of chromium and / or molybdenum, as well as -nitride contains / contain. Security armor according to one of claims 1 to 16, characterized in that the shield ( 1 ) plate-shaped, ie with at least two, in particular substantially parallel to each other, extending top surfaces (D1, D2), which have a larger dimension compared to existing edge surfaces, is formed. Security armor according to one of claims 1 to 17, characterized in that the shield ( 1 ) has a minimum thickness (D) of about 3.0 mm. Security armor according to one of claims 1 to 18, characterized in that the shield ( 1 ) has a maximum thickness (D) in the range of about 10.0 mm to 25.0 mm. Security armor according to one of claims 1 to 19, characterized in that the shield ( 1 ) is treated only partially thermochemically in the area of the top surfaces (D1, D2). Security armor according to one of claims 1 to 20, characterized in that the shield ( 1 ) with a, in particular high-strength, impact-resistant, tear-resistant, chemically resistant, flame-retardant and / or self-extinguishing, coating ( 2 ), such as a protective fabric consisting of para-aramid fibers. A method for producing a security armor for protection against fire, in particular a security armor according to one of claims 1 to 21, wherein a shield ( 1 ) having a thickness (D) consisting of an alloyed steel having a base carbon content of less than 0.3 mass% and by a thermochemical treatment in one of at least one top surface (D1) of the shield ( 1 ) outgoing edge zone (R) enriched with strength-enhancing elements, such as carbon and / or nitrogen, and is subjected to a subsequent thermal treatment, such as curing and / or tempering, characterized in that the steel has a content of silicon of not more than 0.4 Ma .-% and is enriched to at least 0.5 wt .-% carbon in the peripheral zone (R) that is set by the subsequent thermal treatment with carbide formation on the top surface (D1) a minimum hardness of 55 HRC and that corresponding to one each selected depth (t) of the carbon-enriched edge zone (R) after hardening and tempering of the thermochemically treated steel at most about 50% of the thickness (D) of the shield ( 1 ) have substantially the original hardness of the steel or a slightly higher hardness and at least about 50% of the thickness (D) of the shield ( 1 ) have a higher hardness. Method according to claim 22, characterized in that that the thermochemical treatment as a carburization in a Temperature in the range between 900 ° C and 1040 ° C and with a treatment time in the range of 30 to 720 minutes, especially with a gaseous medium, as in a propane-enriched endogas atmosphere or in low pressure with ethane, carried out becomes. Method according to claim 22, characterized in that that the thermochemical treatment is carried out as a carbonitriding. Method according to one of claims 22 to 24, characterized that the shield (D1) of two top surfaces (D1, D2) starting in Edge zones (R) is enriched with carbon, these edge zones (R) comparatively higher Hardness with each same or different carbon content and each be formed with the same or different hardness and with decreasing carbon content in between the margins (R) are low-carbon or low-carbon Pass region (B) of comparatively lower hardness. Method according to one of claims 22 to 25, characterized that the steel, if necessary by repeated repetition of thermochemical treatment, in the marginal zone (s) (R) to at least 0.8% by mass, in particular more than 1.1% by mass up to 3.5% by mass, is enriched with carbon. Method according to one of claims 22 to 26, characterized that the subsequent thermal treatment is austenitization, in particular at a temperature in the range of 800 ° C to 880 ° C, with the following Deterrence, in particular by oil. Method according to Claim 27, characterized that the quench in a quette, i. under pressure of form and Pressurization, takes place. Method according to claim 27 or 28, characterized that austenitization and subsequent deterrence as double hardening carried out being, being in a first hardening process the Austenitisierungstemperatur on the not or only slightly with Carbon enriched area (6) of the steel and in a second curing, the austenitizing temperature on the carbon-enriched Area (6) of the steel is tuned. A method according to any one of claims 27 to 29, characterized in that by the austenitization and the subsequent quenching a hardness of about 60 to 67 HRC on the top surface (s) (D1, D2) of the shield ( 1 ) is set. Method according to one of claims 22 to 30, characterized that the subsequent thermal treatment a tempering, in particular with a start time in the range of up to 3 hours at a temperature in the range up to 300 ° C, includes. Method according to one of claims 22 to 31, characterized in that by tempering a hardness of about 35 to 47 HRC in not or only slightly carburized area (B) of the shield ( 1 ) is set. Use of an alloyed steel containing a base carbon content of less than 0.3% by mass and by a thermochemical Treatment in a marginal zone (R) with strengthening elements, as carbon and / or nitrogen, is enriched, as a material for the production of a security armor for protection against fire, characterized in that the steel has a content of silicon of not more than 0.4% by mass and with a manganese content of at least 0.8 mass% or at least a chromium content of at least 1.0 mass% combined with a content of manganese and molybdenum, as in steels 25 CrMo 4, 17 CrNiMo 6 or X 19 NiCrMo 4, and that the safety armor a bullet resistance according to the classes B3 and higher according to the norms DIN EN 1522 and DIN EN 1523 has. Use according to claim 33, characterized that the carbon content set by enrichment in the Edge zone (R) is at least 0.5 mass% carbon. Use according to claim 33 or 34, characterized that the carbon content set by enrichment in the Peripheral zone (R) is a hypereutectoid Concentration, in particular a concentration of 1.1 Ma .-% to 3.5 mass%. Use according to one of Claims 33 to 35, characterized that the steel is a low or high alloy, chromium, in particular Chromium together with manganese and / or molybdenum, containing steel, such as 25 CrMo 4, 17 CrNiMo6, 13 CrMo 4 5, 16 MnCr 5 BP, 20 MnCr5 or X 19 NiCrMo 4, is. Use according to any one of claims 33 to 36, characterized in that the steel is a low-alloyed, predominantly manganese-containing steel, such as 16 MnCr 5, 16 MnCr 5 BP, 16 MnCrS 5, 20 MnCr 5, 21 MnCr 5, 20 MnCrS 5. Use according to one of Claims 33 to 37, characterized the content of manganese in the steel is greater than about 0.8 mass%, preferably greater than 1.0 mass% but less than about 2.5 mass%, preferably smaller than 2.0 wt%, with the content of manganese being particularly preferred in the range of 1.15% by weight to 1.30% by weight. Use according to one of Claims 33 to 38, characterized that the content of chromium in the steel is not greater than about 1.6% by mass and preferably in the range of 1.15 mass% to 1.30 mass%. Use according to one of Claims 33 to 39, characterized the steel has the following values of the chemical melting analysis: C - 0.17 to 0.20% by mass, Si - 0.20 to 0.30 mass%, Mn - 1.15 to 1.30 mass%, P - maximum 0.030% by mass, S - maximum 0.030% by weight, Al - 0.020 to 0.050 mass%, Cu - maximum 0.25 mass%, Ni - maximum 0.25 mass%, Cr - 1.15 to 1.30 mass%, Ti - 0.02-0.05 mass%, B - 0.0015 to 0.004% by mass. Use according to one of claims 33 to 36, characterized that the steel is a high-alloy, in particular nickel-containing Steel, such as X 19 NiCrMo 4.