GB2035374A

GB2035374A - Steel alloy

Info

Publication number: GB2035374A
Application number: GB7931820A
Authority: GB
Original assignee: Wilkinson Sword Ltd
Current assignee: Wilkinson Sword Ltd
Priority date: 1978-10-19
Filing date: 1979-09-13
Publication date: 1980-06-18
Also published as: CA1136904A; AU5181879A; DE2942015A1; IT1166009B; US4259126A; ZA795584B; IT7909571A0

Description

1

GB 2 035 374 A

1

SPECIFICATION

Improvements in or relating to razor blades

5 This invention relates to razor blades, to the compositions of steel alloys used for the razor blades, and to 5 methods of manufacturing razor blade strip from such steel alloys.

Our British Patent 1 104 932 describes compositions of steel alloys for use for razor blades, and methods of manufacturing razor blades from such compositions.

We have found that there are particular ranges of compositions which lie within the broader ranges 10 disclosed in British Patent 1 104 932 from which improved razor blades can be produced. 10

According to the present invention there is provided a steel alloy, for use for razor blades, whose composition is:

Ni% 15 to 25

15 Cr% 3 to 8 15

Ti% 2 to 5

A1% 1 to 5

with the total of titanium plus aluminium being less than 9%, the balance being iron and impurities, the level 20 of impurities being such that: 20

c%

less than 0.02

Mn%

less than 0.2

Si%

less than 0.2

N%

less than 0.02

P%

less than 0.02

S%

less than 0.02

The invention also provides a steel alloy, for use for razor blades, whose composition is:

30 30

Ni% 17 to 22

Cr% 3.5 to 5

Ti% 3 to 4.5

A1% 2 to 4

35 35

the balance being iron and impurities, the level of impurities being such that:

40 Si% Iessthan0.1 40

C%

less than 0.01

Mn%

less than 0.1

Si%

less than 0.1

N%

less than 0.01

P%

less than 0.01

S%

less than 0.01

45 The invention further provides a steel alloy, for use for razor blades, whose composition is: 45

Ni % 20

Cr% 4

Ti% 4

50 A1 % 3 50

the balance being iron and impurities, the level of impurities being such that:

C% less than 0.005

55 Mn % less than 0.05 55

C%

less than 0.005

Mn %

less than 0.05

Si %

less than 0.05

N %

less than 0.003

P%

less than 0.005

S%

less than 0.005

60 60

There is also provided by the invention a method of manufacturing razor blade strip from an alloy having a composition as aforesaid, in which the alloy is hot forged to produce bar which is rolled, without prior cooling, to produce strip and is held at elevated temperature for a time sufficient to austenitise the structure, the strip is then quenched, descaled, and reduced to final thickness. The ranges of compositions suitable for 65 the present invention are given in the table below, the first column giving the maximum range for the 65

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GB 2 035 374 A

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alloying elements used (the balance being iron). The second column gives a narrower range which we have found to be preferred, whilst in the third column there is given one example of a composition which has been found to be particularly advantageous.

5 Element . ' * . • - Maximum Preferred Example

Range Range

Ni%

15 to 25

17 to 22

20

Cr%

3 to 8

3.5 to 5

4

10Ti%

2 to 5*

3 to 4.5

4

A1%

1 to 5*

2 to 4

3

C%

less than 0.02

0.01

0.005

Mn%

less than 0.2

0.1

0.05

Si%

less than 0.2

0.1

0.05

15 N%

less than 0.02

0.01

0.003

P, S%

less than 0.02

0.01

0.005

*butTi + A1 should be less than 9%

20 The choice of percentages of the elements is determined from the following considerations. The lower level in chromium (3%, preferably 3.5%) is set by the need to have adequate corrosion resistance. The upper limit (8%, preferably 5%) is because strength of the alloy, and ease of fabrication, deteriorate as the chromium content is increased.

Nickel is necessary to enable the alloy to be made fully austenitic at high temperature; sufficient must be 25 there to prevent the formation of 5-ferrite. An upper limit on the nickel content is set because nickel stabilises the austenite against transformation to martensite during cold working and essentially full transformation is required to obtain maximum strength. If a lower level of cold working than 90 to 99% is being used, then the nickel content should be somewhat reduced. Since chromium also stabilises the austenite against martensite transformation, the contents of nickel and chromium should be balanced so that the content of 30 nickel plus chromium is preferably 22 to 26%.

Titanium and aluminium are the main hardening elements. The strength of the alloy decreases as they are reduced, which sets their lower limits. The alloys become difficult to hot work if the alminium and titanium levels exceed the preferred ranges. This is through to be due to the presence of intermetallic compounds which are not fully dissolved in the austenitic phase at high temperature, and which may cause fracture on 35 hot working. The total content of aluminium plus titanium should be less than 9%.

It is important that the residual elements carbon, manganese, silicon, nitrogen, phosphorous and sulphur should be kept at a low level, in common with general practice with maraging steels. Carbon and nitrogen form hard soluble carbides and nitrides with the titanium and aluminium present in the steel resulting in poor ductility, which can result in fracture on processing, and poor strength which can give problems at the 40 cutting edge forming stage. Phosphorous and sulphur should be kept at a low level for similar reasons.

Methods of manufacturing razor blade strip 0.1 mm thick from an alloy having the exemplified composition given in the third column of the table above, will now be described:

Example 1

45 The alloy is produced by vacuum melting.to avoid contamination by residual elements and oxides,

preferably using a two-state process consisting of vacuum melting, followed by consumable arc re-melting which further reduces the proportion of non-metallic elements and reduces segregation. The alloy is homogenised at a temperature in the region of 1200°C and is hot forged at this temperature to produce bar of 75 mm diameter. The bar is next rolled at this temperature to produce strip of 6.5 mm thickness and then 50 held at 1200°Cfor 15 minutes to austenitisethe structure. The strip is quenched into water from the austenitising temperature and the scale removed. The strip is then reduced to its final thickness by cold rolling without intermediate annealing, giving an approximately 98.4% reduction in area. The strip can then be slit to a final width which is appropriate for the cutting-edge forming process. Prior to edge forming the strip is subjected to a hardening treatment as described below. The reduction to final dimensions takes place 55 whilst the material is still relatively soft and priorto the hardening treatment.

Example II

The process differs from Example I by the use, during reduction to final thickness, of intermediate anneals at temperatures of 1050 to 1200°C, to reduce the amount of cold reduction necessary. For example, an anneal 60 could be given when the strip was at 1.00 mm thickness, the final cold reduction in area being 90%.

Example III

The initial stages are the same as for Example!, but instead of hot rolling to form strip the bar is hot rolled at 1200°Cto 5.0 mm diameter rod.His austenitised for 15 minutes at 1200°C and water quenched. The scale 65 is then removed. The rod is next cold drawn to 1.25 mm diameter, either with or without an intermediate

5

10

15

20

25

30

35

40

45

50

55

60

65

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GB 2 035 374 A

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anneal. The wire is then flattened by rolling to produce a strip of 2.0 mm width and 0.1 mm thickness, giving approximately 99% reduction in area if there is no intermediate anneal.

Example IV

5 The initial stages are the same as for Example III, but the alloy is hot rolled to 15.0 mm diameter rod, 5

austenitised for 20 minutes at 1200°C and water quenched. After descaling the alloy is cold drawn to 5.0 mm diameter rod, annealed for 10 minutes at 1150°C and water quenched. It is then cold drawn to 2.6 mm diameter wire and flattened to produce strip of 4.3 mm width and 0.1 mm thickness without further annealing.

10 The austenitising temperatures which may be used are higherthan those contemplated in British Patent 1 10 104932 and may lie within the range of 1050°C to 1250°C with the lower limit preferably 1100°C. Another difference is the preferred use of quenching for reducing the likelihood of precipitates forming during cooling.

Conventional hardening of maraging steels is by ageing for one to two hours at 480°C in an inert 15 atmosphere. For an alloy having the composition given in the third column of the table above such a 15

treatment produces a hardness of 850 to 900 VPN (Vicker's Pyramid Number) for strip rolled to 98% cold reduction in area, but the strip is relatively brittle. With the present invention a shorter time/higher temperature treatment is preferred to improve ductility and has economic advantages. With careful control of the time, a higher level of toughness can be achieved for a given hardness value. The exact time require to 20 give optimum properties at a particular hardening temperature vary to some extent with the previous history 20 of the strip, but will not exceed ten minutes. We have found that satisfactory hardening can be obtained in times of less than a minute at temperatures between 500°C and 600°C, the required time at any temperature being about the time taken to reach peak hardness.

Hardening may be effected by moving strip continuously through a treatment furnace with the time 25 determinedfrom the fact that as hardness increases the toughness (impact energy) decreases. For example 25 a hardness of 850 VPN can be achieved with a toughness which is satisfactory for subsequent processing and use. It will be appreciated that the very short treatment times are economical by comparison with the much longer times customarily employed.

Short treatment times are less advantageous when the impurities (in the form of residual elements) are at 30 a low level. Moreover, conventional hardening, as referred to above, may be used when peak hardness is 30 desired to maximise strength.

Claims

35 1. A steel alloy, for use for razor blades, whose composition is: 35

Ni% 15 to 25

Cr% 3 to 8

Ti% 2 to 5

40 A1% 1 to 5 40

with the total of titanium plus aluminium being less than 9%, the balance being iron and impurities, the level of impurities being such that:

45 C% less than 0.02 45

Mn% less than 0.2

Si% less than 0.2

N% less than 0.02

P% less than 0.02

50 S% less than 0.02 50
2. A steel alloy, for use for razor blades, whose composition is:

Ni% 17 to 22

55 Cr% 3.5 to 5 55

Ti% 3 to 4.5

A1% 2 to 4

the balance being iron and impurities, the level of impurities being such that:

C% less than 0.01

Mn% less than 0.1

Si% less than 0.1

N% less than 0.01

P% less than 0.01

S% less than 0.01

4 GB 2 035 374 A 4
3. A steel alloy according to either claim 1 or claim 2, in which the total of nickel plus chromium is 22 to 26%.
4. A steel alloy, for use for razor blades, whose composition is:

5 Ni% 20 5

Cr% 4

Ti% 4

A1% 3

10 the balance being iron and impurities, the level of impurities being such that: 10

C% less than 0.005

Mn% less than 0.05

Si% less than 0.05

15 N% less than 0.003 15

P% less than 0.005

S% less than 0.005
5. A steel alloy, for use for razor blades, having a composition substantially as described herein.

20
6. Razor strip having a composition in accordance with any one of claims 1 to 5. 20
7. A razor blade of a steel alloy having a composition in accordance with any one of claims 1 to 5.
8. A method of manufacturing razor blade strip from an alloy having a composition in accordance with any one of the preceding claims, in which the alloy is hot forged to produce bar which is rolled, without prior cooling, to produce strip and is held at elevated temperature for a time sufficient to austenitise the structure,

25 the strip is then quenched, descaled, and reduced to final thickness. 25
9. A method according to claim 8, in which instead of the bar being rolled to produce strip it is rolled to produce rod and, after austenitising and descaling, the rod is drawn to wire which is then rolled to strip of final thickness.
10. A method according to either claim 8 or claim 9, in which the alloy is produced by vacuum melting.

30
11. A method according to either claim 8 or claim 9, in which the alloy is produced by vacuum melting 30 followed by consumable arc re-melting.
12. A method according to any one of claims 8 to 11, in which the alloy is homogenised at elevated temperature, for example in the region of 1200°C.
13. A method according to any one of claims 8 to 12, in which the alloy is hot forged at a temperature in

35 the region of 1200°C. 35
14. A method according to any one of claims 8 to 13, in which during reduction to final thickness the material is subjected to intermediate anneals at temperatures in the range 1050 to 1250°C.
15. A method according to any one of claims 8 to 14, in which the strip, at its final thickness, is subjected to hardening at a temperature of between 500 and 600°C for not more than five minutes.

40
16. A method according to claim 15, in which the time is less than one minute. 40
17. A method of manufacturing razor blade strip substantially as described in Example I, II,, III or IV.
18. Razor blade strip manufactured by a method according to anyone of claims 8 to 17.
19. A razor blade manufactured from strip in accordance with claim 18.

Printed for Her Majesty's Stationery Office, by Croydon Printing Company Limited, Croydon Surrey, 1980. Published by the Patent Office, 25 Southampton Buildings, London, WC2A 1AY, from which copies may be obtained.